CN115354237A - Hot-rolled ultrahigh-strength steel plate with tensile strength of 1000MPa and preparation method thereof - Google Patents

Hot-rolled ultrahigh-strength steel plate with tensile strength of 1000MPa and preparation method thereof Download PDF

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CN115354237A
CN115354237A CN202211039248.XA CN202211039248A CN115354237A CN 115354237 A CN115354237 A CN 115354237A CN 202211039248 A CN202211039248 A CN 202211039248A CN 115354237 A CN115354237 A CN 115354237A
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percent
hot
strength
1000mpa
steel plate
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CN115354237B (en
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唐帅
熊杰
蓝慧芳
刘振宇
李建平
王国栋
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Northeastern University China
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations

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

Abstract

A hot-rolled ultrahigh-strength steel plate with 1000 MPa-level tensile strength and a preparation method thereof belong to the technical field of metallurgy. The hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa comprises the following components in percentage by mass: c:0.06 to 0.12 percent; mn:1.0 to 2.0 percent; si:0.08 to 0.2 percent; ti:0.05 to 0.13 percent; cr:0.7 to 1.5 percent; p is less than or equal to 0.02 percent; s is less than or equal to 0.01 percent; the balance of Fe and inevitable impurities. The preparation method comprises the following steps: 1) Smelting the mixture into a casting blank according to the chemical component proportion of the hot rolled steel plate; 2) And (3) preserving the heat of the casting blank, carrying out hot rolling, cooling to a proper temperature at a certain cooling rate, and then raising the temperature on line to coil. The obtained hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa mainly comprises bainite, residual austenite and nano-scale carbide, wherein the carbide is dispersed and distributed on a bainite matrix, the yield strength is not less than 750MPa, the tensile strength is not less than 1000MPa, and the elongation A is not less than 15%.

Description

Hot-rolled ultrahigh-strength steel plate with tensile strength of 1000MPa and preparation method thereof
Technical Field
The invention relates to the technical field of metallurgy, in particular to a hot-rolled ultrahigh-strength steel plate with 1000 MPa-level tensile strength and a preparation method thereof.
Background
In order to achieve the aims of energy conservation, emission reduction and safety, the steel industry is constantly dedicated to developing high-strength steel, and the used materials are required to further improve the strength, so that the purposes of reducing the use amount of steel and realizing light weight are achieved.
The data show an average improvement in fuel economy of about 4.9% for every 10% reduction in total vehicle weight, but every 100kg reduction in vehicle weight results in a 3% to 4.5% increase in safety risk. Therefore, it is necessary to reduce the number of parts and to take the problem of collision safety into consideration, and it is necessary to maintain good plasticity in addition to high strength.
With the rapid development of large-scale and reduced-volume engineering machinery and light weight of automobiles, the demand of hot-rolled ultrahigh-strength steel with the tensile strength of 1000MPa is increasing, and the hot-rolled ultrahigh-strength steel is not only applied to structural members and framework members of automobiles, but also widely applied to chassis members, crawler frame members, members for engineering machinery and the like, and has wide application prospect.
At present, the ultra-high strength steel with the tensile strength of 1000MPa grade can be produced at home and abroad, and according to the existing research, the ultra-high strength steel needs to be obtained by adding hardenability elements such as C, mn, mo and the like, is produced by adopting an on-line/quenching and tempering process, and has the problems of high alloy content, high production cost, low coiling temperature, large control difficulty, long process flow, low plasticity and the like.
The invention patent with the publication number CN101008066B discloses a hot-rolled martensite steel plate with the tensile strength higher than 1000 MPa. The steel plate comprises the following chemical components in percentage by mass: c:0.08 to 0.20; si is less than or equal to 0.8; mn:0.5 to 2.0; al: 0.010-0.060; n is less than or equal to 0.008; p is less than or equal to 0.020; s is less than or equal to 0.005; ti: 0.01E0.03, V is less than or equal to 0.10 and Nb: 0.01-0.05 or more; the others are composed of Fe and unavoidable impurities. The steel plate produced by the method mainly has martensite, adopts low coiling temperature (150 ℃ -Ms), has high strength but low plasticity (the elongation is less than or equal to 9 percent), and simultaneously has high content of Si element which is easy to generate quenching cracks and easy to enrich on the surface of the steel plate to form fayalite (Fe) on the surface 2 SiO 4 ) This affects the surface quality and becomes a crack starting point in bending.
The invention patent with publication number CN109023111B discloses 1000 MPa-grade hot-rolled automobile beam steel and a manufacturing method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: 0.10 to 0.20 percent of C; si is less than or equal to 0.10 percent; mn:1.5 to 1.7 percent; s is less than or equal to 0.005 percent; p is less than or equal to 0.015 percent; nb: 0.045-0.055%; ti:0.08 to 0.10 percent; n is less than or equal to 40ppm; and Als:0.025 to 0.060 percent; h is less than or equal to 0.002 percent; the balance being Fe. The steel plate produced by the method has the structure of martensite and a small amount of ferrite, has higher strength, but has lower elongation percentage of 10-11.5%, adopts a two-stage control cooling process, firstly cools to the intermediate temperature of 600-650 ℃, then quickly cools to 200-300 ℃ for coiling, has low coiling temperature, has higher production process control difficulty and carbon content, is easy to reduce weldability, and increases the cost due to high content of Nb element.
The invention patent with publication number CN109735775A discloses a 1000MPa grade ultra-high strength hot rolled steel strip and a production method thereof, wherein the hot rolled steel strip comprises the following chemical components in percentage by mass: c:0.08 to 0.15 percent; mn:2.30 to 2.83 percent; si is less than or equal to 0.80 percent; and Als:0.025 to 0.052 percent; s is less than or equal to 0.020%; p is less than or equal to 0.030 percent; cr:0.50 to 0.70 percent; ti:0.01 to 0.05 percent; mo:0.15 to 0.30 percent; the balance being Fe and unavoidable impurities. The microstructure of the steel plate produced by the method is ferrite, bainite and martensite, and the steel plate has higher strength and plasticity of 9-14%. However, the method adopts high-content Si and Mn elements, which can increase the difficulty of controlling the surface of the steel plate and become crack starting points during bending processing; the content of Mn exceeds 2.0%, segregation is easy to cause problems of banded structures and the like, the forming performance is influenced, and meanwhile, the production cost is increased due to the high content of Mo element.
The invention patent with publication number CN110331326A discloses a 1000MPa level thin specification hot rolling high-strength double-phase steel plate and a preparation method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: c:0.10 to 0.20 percent; si:0.80 to 1.20 percent; mn:1.20 to 2.0 percent; p: less than or equal to 0.020%; s: less than or equal to 0.010 percent; ti:0.010 to 0.040 percent; cr:0.20 to 0.60 percent; and (3) Als: 0.020-0.060%; the balance of Fe and inevitable impurities. The microstructure of the hot rolled steel plate produced by the method is ferrite and martensite, the yield strength of the product is more than or equal to 550MPa, the tensile strength is more than or equal to 1000MPa, the yield ratio is less than or equal to 0.60, the high tensile strength is achieved, the yield strength is low, the control difficulty of the surface of the steel plate is increased due to the high content of Si element, meanwhile, a three-section control cooling process is adopted, the coiling temperature is low, and the process is accurate and difficult to control.
The invention patent with publication number CN105925896A discloses a 1000MPa grade high-strength high-plasticity hot rolled steel plate and a manufacturing method thereof. The steel plate comprises the following chemical components in percentage by mass: 0.15 to 0.3 percent of C; 5 to 6 percent of Mn; 0.05 to 0.12 percent of N; si <0.2%; s is less than 0.01 percent; p <0.01%; 0.002-0.04% of Al; the balance being Fe. The invention is prepared by steps of smelting, casting, hot rolling, reverse phase transformation annealing and the like, the microstructure is lath austenite and tempered martensite, and the steel has high strength and high elongation, but the welding property is deteriorated due to the addition of high content of C, mn and N elements, and the forming performance is influenced due to the problems of a banded structure caused by Mn element segregation and the like.
The invention patent with publication number CN109207849A discloses a high-strength high-plasticity 1000 MPa-grade hot rolled steel plate and a preparation method thereof. The steel plate comprises the following chemical components in percentage by mass: c:0.05 to 0.40 percent; mn:1.00 to 5.00 percent; si:0.70 to 1.60 percent; al:0.1 to 1.00 percent; nb:0.01 to 0.10 percent; v:0.01 to 0.10 percent; n:0.002 to 0.005 percent; the balance being Fe and unavoidable impurities. The micro-alloy elements of Nb and V are added to combine with C and N to form a nano-scale cluster precipitate to strengthen the matrix structure, so that the strength difference of the two matrix structures (ferrite and martensite) is reduced, the steel plate has high strength and high plasticity, but the yield strength of the steel plate produced by the method is low, and meanwhile, the problems of high difficulty in controlling the surface of the steel plate due to high content of Si element, banded structure and the like due to Mn element segregation affect the forming performance, and the production cost is increased due to more Nb elements.
Through the analysis of the prior art of the 1000MPa hot-rolled ultrahigh-strength steel, the following characteristics exist in the prior art: (1) In order to obtain high strength, a large amount of elements such as C, mn, si and the like are added, so that the surface control difficulty of the steel plate is high, a banded structure is formed to influence the forming performance and the like, or the cost of steel is increased by adding one or more expensive microalloy elements such as Ti, nb, V, mo and the like; (2) The cooling process is complicated or the coiling temperature is low, so that the process is difficult to control accurately; (3) The steel sheet structure is often ferrite + martensite or all martensite, and has high strength but low plasticity.
With the development of nanotechnology, nanomaterials and nanotechnology are introduced into steel materials, and precipitation strengthening and grain refinement of nanoscale precipitated phases are utilized to form one of the most promising strengthening and toughening modes of metal materials, and the method is also the most important strengthening mechanism of novel ultrahigh-strength steel. At present, because the precipitation strengthening effect of single titanium-containing microalloyed steel is limited and the strength level of a steel plate is not high, the development of titanium-containing composite microalloyed steel is concerned more and more.
The disclosed technology of titanium-containing composite microalloyed steel comprises the following steps:
the invention patent of publication No. CN107287519A discloses a vanadium-containing hot-rolled coil for an automobile structure and a production method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: c:0.05 to 0.15 percent; mn:1.2 to 2.0 percent; si is less than or equal to 0.50 percent; nb + V + Ti:0.08 to 0.20 percent; p is less than or equal to 0.035%; s is less than or equal to 0.025 percent; and (3) Als:0.01 to 0.06 percent; the balance being Fe and unavoidable impurities. More Nb, V and Ti microalloy elements are added, and the tensile strength of the produced steel plate is 800MPa.
The invention patent with publication number CN107043890A discloses a hot-rolled automobile steel with the thickness of 1.5-3.0 mm and the yield strength of more than 700MPa and a manufacturing method thereof, and the steel comprises the following chemical components in percentage by mass: c:0.02 to 0.06 percent; mn:1.20 to 2.00 percent; al: 0.010-0.050%; p is less than or equal to 0.01 percent; s is less than or equal to 0.05 percent; nb:0.01 to 0.05 percent; ti:0.05 to 0.12 percent; v:0.05 to 0.20 percent; mo:0.12 to 0.20 percent; the balance of Fe and inevitable impurities; the produced steel plate has yield strength of 700-760 MPa, tensile strength of 760-870 MPa and elongation A of 18-21%.
The invention patent with publication number CN104264052A discloses a steel plate for engineering machinery and a production method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: c:0.05 to 0.09 percent; si:0.05 to 0.30 percent; mn:1.5 to 2.0 percent; p is less than or equal to 0.025 percent; s is less than or equal to 0.005 percent; nb:0 to 0.07 percent; ti:0.08 to 0.15 percent; mo:0.10 to 0.30 percent; and Als:0.015 to 0.06 percent; ca:0.0010 to 0.0030 percent; n is less than or equal to 0.006 percent; the balance being Fe. The thickness of the steel plate is 3.0-8.5 mm, the yield strength of the product is more than or equal to 700MPa, the tensile strength is more than or equal to 785MPa, and the elongation after fracture is more than or equal to 15%.
The invention patent with publication number CN106319389A discloses low-cost and high-machinability steel for engineering machinery and a manufacturing method thereof, and the steel comprises the following components in percentage by mass: c:0.06-0.10%; si:0.30 to 0.60 percent; mn:1.00 to 1.60 percent; p: less than or equal to 0.015 percent; s: less than or equal to 0.0030 percent; ni:0.20 to 0.60 percent; cr:0.50 to 0.80 percent; mo:0.25 to 0.55 percent; v:0.025 to 0.065 percent; b:0.0008 to 0.0020 percent; ti:0.008 to 0.018 percent; al:0.030 to 0.070 percent; n: less than or equal to 0.0050 percent; ca:0.0010 to 0.0040 percent; the balance being Fe and unavoidable impurities. The yield strength of the steel plate produced by the method is more than or equal to 630MPa, and the tensile strength is more than or equal to 700MPa.
In the patents related to titanium-containing composite microalloy reinforced steel, three or more Nb-V-Ti-Mo microalloy elements are added, so that the cost of the steel is increased, and the strength of the produced hot rolled steel plate is lower than 1000MPa, so that the requirement of the current market on the reduction of steel products is difficult to meet.
As described above, in the conventional hot rolled steel sheet having a tensile strength of 1000MPa level, the microstructure mainly includes martensite, and although the tensile strength can reach 1000MPa, the steel sheet has low plasticity and low yield strength, and therefore, there is a need for an ultrahigh strength steel sheet having characteristics of low alloy cost, simple rolling process, higher strength, good plasticity, and the like.
Disclosure of Invention
Aiming at the problems in the prior art, the invention provides a hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa and a preparation method thereof, which adopt a method of rapidly cooling to a bainite region after rolling and then immediately carrying out online heat treatment, in particular realize precipitation strengthening of Ti-Cr composite microalloyed steel through low-cost Ti and Cr microalloying component design and rolling and cooling process control, fully exert the effects of fine-grain strengthening, phase transformation strengthening and precipitation strengthening, and produce the hot-rolled bainite ultrahigh-strength steel, wherein the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa has the yield strength of more than 750MPa, the tensile strength of more than 1000MPa and the elongation after fracture of more than 15 percent, has high yield strength and elongation after fracture while ensuring the high tensile strength, can meet the synchronous improvement of strength and plasticity, and can realize the improvement of the comprehensive performance of steel.
In order to achieve the purpose, the invention adopts the following technical scheme:
the invention provides a hot-rolled ultrahigh-strength steel plate with 1000 MPa-level tensile strength, which comprises the following raw material chemical components in percentage by mass: c:0.06 to 0.12 percent; mn:1.0 to 2.0 percent; si:0.08 to 0.2 percent; ti:0.05 to 0.13 percent; cr:0.7 to 1.5 percent; p is less than or equal to 0.02 percent; s is less than or equal to 0.01 percent; the balance being Fe and unavoidable impurities.
The hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa has a microstructure comprising bainite, residual austenite and nano-scale carbide, wherein the nano-scale carbide is dispersed and distributed on a bainite matrix.
Furthermore, the sum of the volume percentages of the bainite, the residual austenite and the nano-scale carbide is more than or equal to 95 percent, and the size of the nano-scale carbide is mainly 3-20 nm.
The hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa has the yield strength of more than 750MPa, the tensile strength of more than 1000MPa and the elongation after fracture of more than 15 percent.
The thickness of the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa is 2-4 mm.
The selection of chemical components in the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa is determined as follows:
the element C is the least expensive element for improving the strength of the material.
Mn element for remarkably reducing Ar of steel 1 The temperature and the decomposition speed of austenite, mn is a solid solution strengthening element and is in infinite solid solution with Fe, and the strength of the steel can be improved.
Si element is an effective element for improving the strength of a steel sheet without reducing ductility, and is dissolved in ferrite and austenite to improve the strength of the steel. Si can reduce the diffusion speed of carbon in ferrite, so that precipitated carbide is not easy to coarsen.
Ti and C form high-temperature-resistant TiC particles, play a role in precipitation strengthening, pin the original austenite grain boundary, prevent the austenite grains from growing and improve the welding performance.
Cr is a carbide-forming element with moderate affinity with C, cr carbide is uniformly distributed in an iron matrix, the strength of steel is improved through precipitation strengthening, the Cr carbide has the effect of inhibiting the growth of grains under the condition of heating for a short time, the structure can be refined, and the toughness of the steel is enhanced. Meanwhile, in the invention, cr and Ti form composite carbide, which is beneficial to the size refinement of the precipitate, the volume fraction of the precipitate is improved, and the strength and the hardness of the steel plate are improved.
P and S are harmful impurity elements in steel, and P element in steel is likely to segregate at grain boundaries, and the starting point of grain boundary cracking during machining reduces the toughness and bending workability of steel. Since S is present as inclusions such as MnS in steel, the interface between the matrix and the inclusions serves as a starting point of pores during bending of a steel sheet, and the bending workability of the steel sheet is lowered, so that the lower the contents of P and S, the better.
Therefore, the precipitation strengthening of the Ti-Cr composite microalloyed steel is realized by optimally designing alloy components and reasonably avoiding precious components and reasonably proportioning each element, the volume fraction of a nano precipitated phase is increased to the maximum extent, and the strength of the steel plate is increased.
The invention provides a preparation method of a hot-rolled ultrahigh-strength steel plate with 1000 MPa-level tensile strength, which comprises the following steps:
step 1, smelting and blank making:
weighing raw materials according to the chemical components of the raw materials and the mass percentages of the chemical components of the raw materials contained in the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa, and smelting and casting to prepare an ingot; preparing the cast ingot into a plate blank; the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa comprises the following raw material chemical components in percentage by mass: c:0.06 to 0.12 percent; mn:1.0 to 2.0 percent; si:0.08 to 0.2 percent; ti:0.05 to 0.13 percent; cr:0.7 to 1.5 percent; p is less than or equal to 0.02 percent; s is less than or equal to 0.01 percent; the balance of Fe and inevitable impurities;
step 2, hot rolling:
(1) Preserving the heat of the plate blank at 1225 +/-25 ℃ for 2-3 h to obtain a heat-preserved plate blank;
(2) Hot rolling the slab after heat preservation, wherein the initial rolling temperature is 1000-1100 ℃, the final rolling temperature is 830-900 ℃, and the cumulative reduction rate is 90-95% to prepare a hot rolled plate; wherein: before hot rolling, the thickness of the plate blank is 40mm, and after hot rolling, the thickness of the plate blank is 2-4 mm;
(3) The hot rolled plate is cooled to 450-550 ℃ at the cooling rate of 80-150 ℃/s, then is heated to 600 +/-10 ℃ on line and then is coiled, and then is cooled to room temperature after being kept in a heat treatment furnace at 600 +/-10 ℃ for 1h to prepare the hot rolled ultrahigh-strength steel plate with the tensile strength of 1000 MPa.
In the step 1, the ingot is prepared into a slab, and the process comprises the steps of heating the ingot to 1225 +/-25 ℃, preserving heat for 3 hours, forging the ingot into a slab with the thickness of 40mm at 1150 ℃, and then cooling the slab to room temperature in air, wherein the total reduction is 60%.
In the step 2, in the slab heat preservation process, high heat preservation temperature and proper heat preservation time can ensure that alloying elements such as Ti, cr and the like and carbonitrides thereof are completely dissolved, and prevent large-particle precipitated phases from being formed to damage the performance of steel.
In the step 2, in the hot rolling process, the large rolling accumulated reduction rate is adopted to be 90-95%, so that the material is deformed in an austenite recrystallization region and a non-recrystallization region, austenite grains are refined, dislocation in deformed austenite is increased, and the structure is refined after phase transformation.
In the step 2, the hot rolled steel plate is rapidly cooled to 450-550 ℃ at the cooling rate of 80-150 ℃/s, and then is heated to 600 +/-10 ℃ on line for coiling. By controlling the cooling condition and the heating temperature, precipitates are inhibited from being separated out and growing up in the cooling process, a large amount of Ti-Cr composite microalloy nanoscale precipitated phases are promoted to be separated out in the online heat treatment and isothermal processes, the precipitation strengthening effect is enhanced, and the strength of the steel plate is improved.
The invention has the following beneficial effects:
(1) The invention adopts Ti and Cr microalloying mode, has better precipitation strengthening and fine grain strengthening effects in steel, does not contain noble metals such as Ni, mo and the like, and has lower alloy cost;
(2) The method has the advantages of simple process flow, mass production, economy, easiness and the like, and can meet the industrial requirement;
(3) The steel plate provided by the invention has the advantages that the yield strength is more than 750MPa, the tensile strength is more than 1000MPa, the elongation after fracture is more than 15%, and the steel plate has high strong plasticity;
(4) The invention also has the characteristics of stable mechanical property, strong adaptability and the like, and the mechanical property of the product meets the requirement of light weight in the market.
Drawings
FIG. 1 shows the metallographic structure of a hot-rolled ultrahigh-strength steel sheet having a tensile strength of 1000MPa prepared in example 1 of the present invention;
FIG. 2 is a phase center dark field image of a precipitated phase in TEM of a hot rolled ultra-high strength steel plate with a tensile strength of 1000MPa prepared in example 1 of the present invention.
Detailed Description
In the following examples, the melting furnace was an 80kg vacuum induction melting furnace.
In the following examples, the hot rolling mill used was a phi 450mm reversible hot rolling mill.
The technical solutions in the embodiments of the present invention will be described below with reference to the drawings in the embodiments of the present invention. However, the described embodiments represent only a few embodiments of the invention, not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
It should be noted that the embodiments and features of the embodiments may be combined with each other without conflict.
The invention is further described with reference to the following drawings and specific examples, which are not intended to be limiting.
Example 1
A hot-rolled ultrahigh-strength steel plate with 1000 MPa-level tensile strength comprises the following raw material chemical components in percentage by mass: 0.12 percent; mn:1.8 percent; si:0.08 percent; ti:0.13 percent; cr:0.7 percent; p:0.004 percent; s:0.006%; the balance being Fe and unavoidable impurities.
In this embodiment, the method for preparing the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa includes the following steps:
(1) After raw materials are selected according to the chemical components of the raw materials of the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa, the raw materials are smelted and cast into an ingot, and the ingot comprises the following chemical components in percentage by mass: 0.12 percent; mn:1.8 percent; si:0.1 percent; ti:0.13 percent; cr:0.7 percent; p:0.004%; s:0.006%; the balance of Fe and inevitable impurities; heating the cast ingot to 1225 +/-25 ℃, preserving heat for 3 hours, forging the cast ingot into a 40mm thick plate blank at 1150 ℃, and then cooling the plate blank to room temperature in air, wherein the total reduction is 60%.
(2) Heating and preserving the forged plate blank in a heating furnace at the temperature of 1250 ℃ for 2.5h to obtain a heat-preserved plate blank;
(3) Continuously hot rolling the heat-insulated plate blank, wherein the initial rolling temperature is 1100 ℃, the final rolling temperature is 900 ℃, the rolling accumulated reduction rate is 90 percent, and the thickness of the steel plate after rolling is 4mm;
(4) And cooling the hot-rolled steel plate to 450 ℃ at a cooling rate of 80 ℃/s, then heating to 610 ℃ on line for coiling, then carrying out isothermal treatment in a 600 ℃ heat treatment furnace for 1h, and then cooling to room temperature to obtain the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000 MPa.
The mechanical properties of the 1000 MPa-grade hot-rolled ultrahigh-strength steel plate prepared in the embodiment are detected, the yield strength is 756MPa, the tensile strength is 1079MPa, and the elongation after fracture is 16.8%.
The metallographic structure of the 1000 MPa-level hot-rolled ultrahigh-strength steel plate prepared in this example is shown in fig. 1, the microstructure thereof is a granular bainite structure, residual austenite and nano-scale carbide, and the sum of the volume percentages of bainite, residual austenite and nano-scale carbide is 95%; the dark field image of the center of the precipitate under the transmission electron microscope is shown in figure 2, so that nano-scale carbides are dispersed on the bainite matrix, and the size range of the nano-scale carbides is mainly 3-20 nm.
Example 2
A hot-rolled ultrahigh-strength steel plate with 1000 MPa-level tensile strength comprises the following raw material chemical components in percentage by mass: 0.1 percent; mn:1.5 percent; si:0.12 percent; ti:0.05 percent; cr:1.5 percent; p:0.005 percent; s:0.005 percent; the balance of Fe and inevitable impurities.
In this embodiment, the method for preparing a hot-rolled ultrahigh-strength steel sheet having a tensile strength of 1000MPa includes the steps of:
(1) After selecting and matching raw materials according to the chemical components of the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa, smelting the raw materials into an ingot, wherein the chemical components comprise the following components in percentage by mass: 0.1 percent; mn:1.5 percent; si:0.12 percent; ti:0.05 percent; cr:1.5 percent; p:0.005 percent; s:0.005 percent; the balance of Fe and inevitable impurities; heating the cast ingot to 1225 +/-25 ℃, preserving heat for 3 hours, forging the cast ingot into a 40mm thick plate blank at 1150 ℃, and then cooling the plate blank to room temperature in air, wherein the total reduction is 60%.
(2) Heating the forged plate blank in a heating furnace at 1200 ℃ for 2h to obtain a heat-insulated plate blank;
(3) Continuously hot rolling the slab subjected to isothermal heating, wherein the initial rolling temperature is 1000 ℃, the final rolling temperature is 830 ℃, the rolling accumulated reduction rate is 92.5%, and the thickness of the steel plate after rolling is 3mm;
(4) And cooling the hot-rolled steel plate to 500 ℃ at a cooling rate of 90 ℃/s, then heating the steel plate to 600 ℃ on line for coiling, carrying out isothermal treatment in a 600 ℃ heat treatment furnace for 1h, and then cooling the steel plate to room temperature to obtain the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000 MPa.
The hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa prepared in the embodiment has the yield strength of 768MPa, the tensile strength of 1090MPa and the elongation after fracture of 16.2%.
The hot-rolled ultrahigh-strength steel plate of 1000MPa grade prepared by the embodiment has a microstructure comprising granular bainite structure, residual austenite and nano-scale carbide, wherein the size range of the nano-scale carbide is mainly 5-15 nm.
Example 3
A hot-rolled ultrahigh-strength steel plate with 1000 MPa-level tensile strength comprises the following raw material chemical components in percentage by mass: 0.06 percent; mn:1.9 percent; si:0.1 percent; ti:0.1 percent; cr:1.0 percent; p:0.004 percent; s:0.005 percent; the balance of Fe and inevitable impurities.
The preparation method of the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa in the embodiment comprises the following steps:
(1) After raw materials are selected according to the chemical components of the raw materials of the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa, the raw materials are smelted into an ingot, and the ingot comprises the following chemical components in percentage by mass: 0.06 percent; mn:1.9 percent; si:0.1 percent; ti:0.1 percent; cr:1.0 percent; p:0.004 percent; s:0.005 percent; the balance of Fe and inevitable impurities; heating the cast ingot to 1225 +/-25 ℃, preserving heat for 3 hours, forging the cast ingot into a 40mm thick plate blank at 1150 ℃, and then cooling the plate blank to room temperature in air, wherein the total reduction is 60%.
(2) Heating the forged plate blank in a heating furnace at 1225 ℃ for 3h to obtain a heat-insulated plate blank;
(3) Continuously hot rolling the slab subjected to isothermal heating, wherein the initial rolling temperature is 1050 ℃, the final rolling temperature is 880 ℃, the rolling accumulated reduction rate is 95%, and the thickness of the steel plate after rolling is 2mm;
(4) And cooling the hot-rolled steel plate to 550 ℃ at the cooling rate of 150 ℃/s, then heating to 590 ℃ on line for coiling, carrying out isothermal treatment in a 600 ℃ heat treatment furnace for 1h, and then cooling to room temperature to obtain the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000 MPa.
The hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa prepared in the embodiment has the yield strength of 800MPa, the tensile strength of 1147MPa and the elongation after fracture of 15.4%.
The 1000 MPa-level hot-rolled ultrahigh-strength steel plate prepared by the embodiment has a microstructure comprising a granular bainite structure, residual austenite and nano-scale carbides, wherein the size range of the nano-scale carbides is mainly 4-16 nm.
Example 4
A hot-rolled ultrahigh-strength steel plate with 1000 MPa-level tensile strength comprises the following raw material chemical components in percentage by mass: 0.08 percent; mn:1.8 percent; si:0.19 percent; ti:0.08%; cr:1.0 percent; p:0.006%; s:0.005 percent; the balance of Fe and inevitable impurities.
In this embodiment, the method for preparing the hot-rolled ultrahigh-strength steel plate having the tensile strength of 1000MPa includes the following steps:
(1) After raw materials are selected according to the chemical components of the raw materials of the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa, the raw materials are smelted into an ingot, and the ingot comprises the following chemical components in percentage by mass: 0.08%; mn:1.8 percent; si:0.19 percent; ti:0.08 percent; cr:1.0 percent; p:0.006%; s:0.005 percent; the balance of Fe and inevitable impurities; heating the cast ingot to 1225 +/-25 ℃, preserving heat for 3 hours, then forging the cast ingot into a 40mm thick plate blank at 1150 ℃, and then air-cooling the plate blank to the room temperature, wherein the total reduction is 60%.
(2) Heating the forged plate blank in a heating furnace at 1220 ℃ for 3h to obtain a heat-insulated plate blank;
(3) Continuously hot rolling the slab subjected to isothermal heating, wherein the initial rolling temperature is 1040 ℃, the final rolling temperature is 890 ℃, the rolling accumulated reduction rate is 95%, and the thickness of the steel plate after rolling is 2mm;
(4) And cooling the hot-rolled steel plate to 550 ℃ at a cooling rate of 150 ℃/s, heating the steel plate to 600 ℃ on line for coiling, carrying out isothermal treatment in a 600 ℃ heat treatment furnace for 1h, and cooling the steel plate to room temperature to obtain the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000 MPa.
The 1000 MPa-grade hot-rolled ultrahigh-strength steel plate prepared in the embodiment has the yield strength of 800MPa, the tensile strength of 1147MPa and the elongation after fracture of 15.9%.
The hot-rolled ultrahigh-strength steel plate of 1000MPa grade prepared by the embodiment has a microstructure comprising granular bainite structure, residual austenite and nano-scale carbide, wherein the size range of the nano-scale carbide is mainly 6-10 nm.
Comparative example 1
A steel sheet, which is different from example 1 in that:
in the step (2), the heat preservation temperature of the plate blank is 1150 ℃, the heat preservation time is 2.5 hours, because the heat preservation temperature of the plate blank is too low, the alloy elements and the carbides thereof are not completely dissolved, large-particle precipitated phases are formed, the volume fraction of the nano-scale carbides in the subsequent isothermal process is reduced, and the performance of the steel plate is damaged.
Comparative example 2
A steel sheet, which is different from example 1 in that:
in the step (2), the slab heat preservation temperature is 1280 ℃, the heat preservation time is 2 hours, and because the slab heat preservation temperature is too high, austenite grains are coarse, the final structure is coarse, and the performance of the steel plate is damaged.
Comparative example 3
A steel sheet, which is different from example 1 in that:
in the step (3), the initial rolling temperature is 960 ℃, the final rolling temperature is 798 ℃, and the cumulative reduction rate is 90%, because the initial rolling temperature and the final rolling temperature are too low in the hot rolling process, the grain refinement is insufficient in the austenite recrystallization process, the grain size is not uniform, the final structure is affected, and the performance of the steel plate is damaged.
Comparative example 4
A steel sheet, which is different from example 1 in that:
in the step (3), the cumulative reduction is 80%, and since the cumulative reduction is low during hot rolling, the austenite is not sufficiently deformed in the recrystallized and unrecrystallized regions, the austenite grains are not significantly refined, and the final structure is coarse, resulting in a reduction in the performance of the steel sheet.
Comparative example 5
A steel sheet, which is different from example 1 in that:
in the step (4), the steel plate is rapidly cooled to 550 ℃ at a cooling rate of 60 ℃/s, then is heated to 650 ℃ on line for coiling, because the control of the cooling process after hot rolling is very critical to phase change, if the cooling speed is low, the phase change driving force is insufficient, bainite laths after phase change are thick, the performance of the steel plate is reduced, and if the coiling temperature is too high, the size of carbides precipitated in the coiling process of the steel plate is large, and the performance of the steel plate is seriously damaged.
In the invention, after hot rolling, the steel plate is rapidly cooled to a bainite region, and then is heated to 600 ℃ for isothermal treatment, so that the Ti-Cr composite micro alloy is precipitated in the isothermal treatment to enhance the precipitation strengthening effect, and the strength of the steel plate is improved.
Comparative example 6
A steel sheet, which is different from example 1 in that:
in the step (4), the steel sheet is rapidly cooled to 400 ℃ at a cooling rate of 60 ℃/s, and then is heated online to 600 ℃ for coiling, and because the cooling rate and the final cooling temperature are too low, a martensite structure is easily formed, and the structure is coarse, so that the performance of the steel sheet is damaged.
Comparative example 7
A steel sheet, which is different from example 1 in that:
the Si content is 0.7%, the Mn content is 2.0%, the control difficulty of the steel plate surface is high due to the high Si content, the problems of banded structures and the like caused by Mn element segregation are solved, and the yield strength is low.
Comparative example 8
A steel sheet, which is different from example 1 in that:
and the Ti element is not contained, austenite grains are easy to be coarse in the slab reheating process, the performance of a steel plate is deteriorated, the precipitation of carbides in the subsequent isothermal process is not facilitated, and the precipitation strengthening effect is reduced.
Comparative example 9
A steel sheet, which is different from example 1 in that:
and Cr is not contained, only Ti-containing carbide is precipitated in the isothermal process, the number of the carbide is reduced, the size of the carbide is larger, and the precipitation strengthening effect is reduced.
The above description is only an example of the present invention and is not intended to limit the scope of the present invention, and it should be understood that those skilled in the art should be able to recognize that the invention is included within the scope of the present invention by equivalent substitution and obvious change made from the description and the drawings of the present invention.

Claims (7)

1. The hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa is characterized by comprising the following raw material chemical components in percentage by mass: c:0.06 to 0.12 percent; mn:1.0 to 2.0 percent; si:0.08 to 0.2 percent; ti:0.05 to 0.13 percent; cr:0.7 to 1.5 percent; p is less than or equal to 0.02 percent; s is less than or equal to 0.01 percent; the balance being Fe and unavoidable impurities.
2. The hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa according to claim 1, wherein the microstructure of the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa is bainite, retained austenite and nano-scale carbides, and the nano-scale carbides are dispersedly distributed on a bainite matrix.
3. The hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa grade according to claim 2, characterized in that the sum of the volume percentages of bainite, retained austenite and nano-scale carbide is more than or equal to 95%, and the size of the nano-scale carbide is mainly 3-20 nm.
4. The hot-rolled ultrahigh-strength steel sheet having a tensile strength of 1000MPa according to claim 1, wherein the yield strength of the hot-rolled ultrahigh-strength steel sheet having a tensile strength of 1000MPa or more is 750MPa or more, the tensile strength is 1000MPa or more, and the elongation after fracture is 15% or more.
5. The hot-rolled ultrahigh-strength steel sheet having a tensile strength of 1000MPa level according to claim 1, wherein the thickness of the hot-rolled ultrahigh-strength steel sheet having a tensile strength of 1000MPa level is 2 to 4mm.
6. The method for producing a hot-rolled ultrahigh-strength steel sheet having a tensile strength of 1000MPa level according to any one of claims 1 to 5, comprising the steps of:
step 1, smelting and blank making:
weighing raw materials according to the raw material chemical components contained in the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa and the mass percentage of each raw material chemical component, and smelting and casting to prepare an ingot; preparing the cast ingot into a plate blank; the hot-rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa comprises the following raw material chemical components in percentage by mass: c:0.06 to 0.12 percent; mn:1.0 to 2.0 percent; si:0.08 to 0.2 percent; ti:0.05 to 0.13 percent; cr:0.7 to 1.5 percent; p is less than or equal to 0.02 percent; s is less than or equal to 0.01 percent; the balance of Fe and inevitable impurities;
step 2, hot rolling:
(1) Preserving the heat of the plate blank at 1225 +/-25 ℃ for 2-3 h to obtain a heat-preserved plate blank;
(2) Hot rolling the plate blank after heat preservation, wherein the initial rolling temperature is 1000-1100 ℃, the final rolling temperature is 830-900 ℃, and the accumulated reduction rate is 90-95 percent to prepare a hot rolled plate; wherein: the thickness of the plate blank is 40mm before hot rolling, and the thickness of the plate blank is 2-4 mm after hot rolling;
(3) The hot rolled plate is cooled to 450-550 ℃ at the cooling rate of 80-150 ℃/s, then is heated to 600 +/-10 ℃ on line and coiled, and then is kept in a heat treatment furnace at the temperature of 600 +/-10 ℃ for 1h and cooled to room temperature, so that the hot rolled ultrahigh-strength steel plate with the tensile strength of 1000MPa is prepared.
7. The method for preparing a hot-rolled ultrahigh strength steel sheet according to claim 6, wherein in the step 1, the ingot is prepared into a slab by heating the ingot to 1225 ± 25 ℃ for 3 hours, forging the ingot at 1150 ℃ to form a slab 40mm thick, and air-cooling the slab to room temperature with a total reduction of 60%.
CN202211039248.XA 2022-08-29 2022-08-29 Hot-rolled ultrahigh-strength steel plate with tensile strength of 1000MPa and preparation method thereof Active CN115354237B (en)

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