CN119685696A - High-strength steel and its preparation method and application, automotive slide rail - Google Patents
High-strength steel and its preparation method and application, automotive slide rail Download PDFInfo
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- 239000010959 steel Substances 0.000 title claims abstract description 104
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- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims abstract description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 6
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 239000010703 silicon Substances 0.000 claims abstract description 6
- 239000011593 sulfur Substances 0.000 claims abstract description 6
- 239000010936 titanium Substances 0.000 claims abstract description 6
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 6
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- 239000011574 phosphorus Substances 0.000 claims abstract description 5
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims abstract description 4
- 238000011282 treatment Methods 0.000 claims description 67
- 238000000034 method Methods 0.000 claims description 29
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- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 24
- 238000000137 annealing Methods 0.000 claims description 20
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- 238000001816 cooling Methods 0.000 claims description 15
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- 229910045601 alloy Inorganic materials 0.000 claims description 13
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- 239000001257 hydrogen Substances 0.000 claims description 4
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- 229910000859 α-Fe Inorganic materials 0.000 claims description 4
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical group C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims description 3
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- 238000009826 distribution Methods 0.000 abstract description 7
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Abstract
本发明涉及一种高强度钢及其制备方法与应用、汽车用滑轨，按照质量百分数计，所述高强度钢的组分为：0.04％～0.1％碳、0.1％～0.25％硅、0.8％～1.3％锰、0～0.005％硫、0～0.02％磷、0.01％～0.035％钒、0.1％～0.15％钛、0.02％～0.06％酸溶铝、0＜氮≤0.007％、余量Fe和不可避免的杂质元素。该钢材的各向同性差异小，组织分布更均匀，兼具高强度和较好的延伸率。
The present invention relates to a high-strength steel and a preparation method and application thereof, and a slide rail for automobiles. The components of the high-strength steel are, by mass percentage, 0.04% to 0.1% carbon, 0.1% to 0.25% silicon, 0.8% to 1.3% manganese, 0 to 0.005% sulfur, 0 to 0.02% phosphorus, 0.01% to 0.035% vanadium, 0.1% to 0.15% titanium, 0.02% to 0.06% acid-soluble aluminum, 0 < nitrogen ≤ 0.007%, the remainder Fe and inevitable impurity elements. The steel has a small isotropy difference, a more uniform tissue distribution, and has both high strength and good elongation.
Description
Technical Field
The invention relates to the technical field of alloys, in particular to high-strength steel, a preparation method and application thereof and a sliding rail for an automobile.
Background
In recent years, in order to meet the requirements of light weight, energy saving and emission reduction of automobiles, each automobile part is kept high in strength while the weight is reduced as much as possible, and thus steel is one of important materials for automobile parts. However, some of the automobile parts as precision parts are required to have high dimensional accuracy and surface quality, for example, a slide rail is an important precision part on an automobile seat, and a common slide rail is mainly installed under the seat, so that a mechanism for adjusting the front, rear, left and right positions is required to have several key characteristics, namely safety characteristics, connection characteristics, supporting characteristics and adjusting characteristics, namely, high strength and good extensibility are required to be simultaneously achieved. However, conventional steels mainly exhibit high strength properties, and how to obtain steels having both high strength and good elongation is still a challenge.
Thus, there is a need in the art for improvement.
Disclosure of Invention
Based on the above, the invention provides high-strength steel with high strength and good elongation, a preparation method and application thereof, and an automobile sliding rail.
According to one aspect of the invention, the high-strength steel comprises, by mass, 0.04% -0.1% of carbon, 0.1% -0.25% of silicon, 0.8% -1.3% of manganese, 0% -0.005% of sulfur, 0% -0.02% of phosphorus, 0.01% -0.035% of vanadium, 0.1% -0.15% of titanium, 0.02% -0.06% of acid-soluble aluminum, 0< nitrogen being less than or equal to 0.007%, and the balance of Fe and unavoidable impurity elements.
The high strength steel may have a yield strength of greater than 800MPa, a tensile strength of greater than 830MPa, and an elongation of greater than 10%.
In some of these embodiments, the high strength steel structure includes ferrite, martensite, austenite, and cementite structures.
In some embodiments, the high strength steel has a thickness of 1.2mm to 2mm.
In another aspect of the present invention, there is provided a method for preparing high strength steel, comprising the steps of:
Providing preparation raw materials according to the above-mentioned metering ratio of components of high-strength steel, and making the preparation raw materials into alloy melt by means of smelting treatment and refining treatment in turn;
And (3) carrying out casting treatment, hot rolling treatment, cold rolling treatment and annealing treatment on the alloy melt in sequence to obtain the high-strength steel.
In the preparation method of the high-strength steel, the alloy melt is prepared by smelting and refining the preparation raw materials according to the stoichiometric ratio of the high-strength steel, and then the hot rolling treatment, the cold rolling treatment and the annealing treatment are sequentially carried out after the casting treatment, so that a hot rolling pearlite structure is obtained, and then particles with a strong strengthening effect are separated out during the annealing, the strength is improved, and meanwhile, the phase-change stress is released, so that the isotropy difference of the steel is small, the structure distribution is more uniform, the performance difference of each part is small, and the high-strength and better extensibility are achieved.
In some of these embodiments, prior to the step of performing the refining process, the method further comprises the steps of:
carrying out ladle argon blowing treatment on the prepared alloy melt subjected to smelting treatment;
in the step of ladle argon blowing treatment, controlling the temperature of the end point of an argon station to be more than 1542 ℃ and/or
The refining treatment temperature is 1570-1590 ℃ and the refining treatment time is 40-120 minutes.
In some of these embodiments, the hot rolling process includes the steps of:
the slab subjected to the casting treatment is rolled after being subjected to heating treatment, wherein the initial rolling temperature is 1090-1150 ℃, and the final rolling temperature is 850-900 ℃;
wherein the heating treatment time is not less than 25min.
In some embodiments, the conditions of the cold rolling treatment comprise controlling the single-pass reduction rate of a single stand to be more than or equal to 15 percent, 3-5-pass reciprocating rolling at a rolling speed of 200-350 m/min, and/or
The annealing treatment conditions comprise that a hood-type annealing furnace is adopted to execute a hydrogen blowing system, and the temperature is kept at 400 ℃, 520 ℃ and 600 ℃ for 2 hours, 2 hours and 10 hours respectively.
In some of these embodiments, after the step of hot rolling treatment and before the step of cold rolling treatment, the method further comprises the steps of:
Sequentially carrying out laminar cooling and pickling treatment on the plate blank subjected to the hot rolling treatment, wherein the final cooling temperature of laminar cooling is 590-640 ℃, the pickling treatment speed is 30-120 m/min, and/or
After the step of annealing treatment, further comprising the steps of:
and carrying out flattening treatment on the plate blank subjected to the annealing treatment, wherein the rolling force is controlled to be 300+/-100 tons in the flattening treatment process.
In the preparation method, the conditions of each rolling step are further controlled, so that hardening measures such as solid solution strengthening, precipitation strengthening, dislocation strengthening, fine grain strengthening and the like are completed for each specific component, crystal grains with proper size are obtained by high-temperature deformation recrystallization of an austenite region, deformation of a low-temperature austenite unrecrystallized region and laminar cooling after rolling, stable and uniform strengthening tissues are obtained by annealing, and the performance of the steel is further improved.
In still another aspect, the invention further provides the use of the high-strength steel or the high-strength steel prepared by the preparation method of the high-strength steel in the preparation of automobile parts.
In still another aspect of the present invention, there is also provided a sliding rail for an automobile, which includes the above-mentioned high-strength steel or the high-strength steel manufactured by the above-mentioned method for manufacturing high-strength steel.
The steel has small isotropy difference, more uniform tissue distribution, small performance difference at all parts, high strength and better elongation, small thickness tolerance when being manufactured into a steel plate, high control precision, and the thickness precision can reach +/-20 mu m when the target thickness is less than or equal to 2mm.
Drawings
Fig. 1 is a metallographic structure diagram of the surface layer of the high-strength steel coil prepared in example 1;
FIG. 2 is a metallographic structure diagram of a section of 1/4 thickness of the high-strength steel coil prepared in example 1;
FIG. 3 is a metallographic structure diagram of a section of 1/2 thickness of the high-strength steel coil prepared in example 1.
Detailed Description
The present invention will be described more fully hereinafter in order to facilitate an understanding of the present invention. Preferred embodiments of the invention are given in the detailed description. This invention may, however, be embodied in many different forms and should not be construed as limited to the embodiments set forth herein. Rather, these embodiments are provided so that this disclosure will be thorough and complete.
Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. The terminology used herein in the description of the invention is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention. The term "and/or" as used herein includes any and all combinations of one or more of the associated listed items.
Terminology
Unless otherwise indicated or contradicted, terms or phrases used herein have the following meanings:
The term "and/or," "and/or," as used herein, includes any one of two or more of the listed items in relation to each other, as well as any and all combinations of the listed items in relation to each other, including any two of the listed items in relation to each other, any more of the listed items in relation to each other, or all combinations of the listed items in relation to each other. It should be noted that, when at least three items are connected by a combination of at least two conjunctions selected from the group consisting of "and/or", "and/or", it should be understood that, in the present application, the technical solutions include technical solutions that all use "logical and" connection, and also include technical solutions that all use "logical or" connection. For example, "a and/or B" includes a combination of A, B and a and B in three parallel schemes. For another example, the technical schemes of "a, and/or B, and/or C, and/or D" include any one of A, B, C, D (i.e., the technical schemes of all "logical or" connections), also include any and all combinations of A, B, C, D, i.e., the combinations of any two or three of A, B, C, D, and also include four combinations of A, B, C, D (i.e., the technical schemes of all "logical and" connections).
In the present application, when at least three features are connected by a combination of at least two conjunctions selected from the group consisting of "and/or", "and/or", the expression "having one or more features" corresponds to, for example, "TA, and/or, TB, and/or, TC, and/or, TD" corresponds to "having one or more features of TA, TB, TC, and TD".
The term "plural", and the like in the present invention refers to, unless otherwise specified, a number of 2 or more. For example, "one or more" means one kind or two or more kinds.
As used herein, "a combination thereof," "any combination thereof," and the like include all suitable combinations of any two or more of the listed items.
In the present invention, "optional" means optional or not, that is, means any one selected from two parallel schemes of "with" or "without". If multiple "alternatives" occur in a technical solution, if no particular description exists and there is no contradiction or mutual constraint, then each "alternative" is independent.
In the present invention, the terms "first", "second", "third", "fourth", etc. are used for descriptive purposes only and are not to be construed as indicating or implying a relative importance or quantity, nor as implying an importance or quantity of a technical feature being indicated. Moreover, the terms "first," "second," "third," "fourth," and the like are used for non-exhaustive list description purposes only, and are not to be construed as limiting the number of closed forms.
In the invention, the technical characteristics described in an open mode comprise a closed technical scheme composed of the listed characteristics and also comprise an open technical scheme comprising the listed characteristics.
In the present invention, a numerical range (i.e., a numerical range) is referred to, and, unless otherwise indicated, a distribution of optional values within the numerical range is considered to be continuous and includes two numerical endpoints (i.e., a minimum value and a maximum value) of the numerical range, and each numerical value between the two numerical endpoints. When a numerical range merely points to integers within the numerical range, unless expressly stated otherwise, both endpoints of the numerical range are inclusive of the integer between the two endpoints, and each integer between the two endpoints is equivalent to the integer directly recited. When multiple numerical ranges are provided to describe a feature or characteristic, the numerical ranges may be combined. In other words, unless otherwise indicated, the numerical ranges disclosed herein are to be understood as including any and all subranges subsumed therein. The "numerical value" in the numerical interval may be any quantitative value, such as a number, a percentage, a proportion, or the like. "numerical interval" is allowed to broadly include numerical interval types such as percentage intervals, proportion intervals, ratio intervals, and the like.
The temperature parameter in the present invention is not particularly limited, and may be a constant temperature treatment or may vary within a predetermined temperature range. It should be appreciated that the constant temperature process described allows the temperature to fluctuate within the accuracy of the instrument control. Allows for fluctuations in a range such as + -5 deg.C, + -4 deg.C, + -3 deg.C, + -2 deg.C, + -1 deg.C.
In the present invention, the term "room temperature" or "normal temperature" generally refers to 4 ℃ to 35 ℃, for example 20±5 ℃. In some embodiments of the present invention, "room temperature" or "normal temperature" refers to 10 ℃ to 30 ℃. In some embodiments of the present invention, "room temperature" or "normal temperature" refers to 20 ℃ to 30 ℃.
The mass or weight of the related components mentioned in the description of the embodiments of the present invention may refer not only to the specific content of each component, but also to the proportional relationship of the mass or weight of each component, so long as the content of the related component in the description of the embodiments of the present invention is scaled up or down within the scope of the disclosure of the embodiments of the present invention. Specifically, the mass or weight described in the specification of the embodiment of the present invention may be a unit well known in the chemical industry such as mu g, mg, g, kg.
The embodiment of the invention provides high-strength steel, which comprises, by mass, 0.04% -0.1% of carbon, 0.1% -0.25% of silicon, 0.8% -1.3% of manganese, 0% -0.005% of sulfur, 0% -0.02% of phosphorus, 0.01% -0.035% of vanadium, 0.1% -0.15% of titanium, 0.02% -0.06% of acid-soluble aluminum, 0< nitrogen not more than 0.007%, and the balance of Fe and unavoidable impurity elements.
The high-strength steel contains components in a specific proportion, and the influence of each specific element on the performance of the steel is beneficial and disadvantageous, and a great number of creative experimental researches show that carbon is an effective element for improving the strength of the steel, but the excessively high C content can reduce the low-temperature toughness and deteriorate the welding performance and the corrosion resistance; silicon can reduce the solubility of carbon in austenite, reduce the stability of supercooled austenite, accelerate the transformation process, play a solid solution strengthening role, improve the elongation of a steel plate, balance the strength and plasticity of the steel plate, manganese can improve the hardenability and improve the strength of a material, but because Mn is a positive segregation element which is easy to produce a banded structure, the Mn content is not suitable for being excessively high, sulfur is a harmful element in high-strength steel and is easy to produce MnS segregation and sulfide inclusion, so that the sulfur content needs to be controlled, on one hand, the quantity and the size of sulfide inclusion can be reduced, and the sulfide (mainly MnS) form can be modified, long-strip sulfide is avoided, punching is avoided, phosphorus is also a harmful element in the high-strength steel, while P, S and Mn are used together, the cutting performance of the steel can be improved, the surface quality of a machined part is improved, but the P element is dissolved in ferrite, the strength and the hardness of the steel are improved, the biggest harmful part is serious, the increased brittleness is increased, the plasticity and toughness of the steel are obviously reduced, so that the steel is easy to be cracked when cold working, the vanadium is an excellent deoxidizer, the specific content can be increased, the grain size of the aluminum can be formed under high-strength and the high-strength aluminum carbide, the high-strength steel is easy to be damaged by the high-toughness, and the high-strength aluminum carbide can be formed by the high-strength alloy steel, and the high-strength carbon grain corrosion resistance can be easily improved, titanium and nitrogen are combined to form TiN, the existence of the TiN can inhibit coarsening of crystal grains in a welding heat affected zone, meanwhile, nitrogen can be combined with elements such as aluminum, vanadium and the like to form extremely stable nitride, and a precipitation strengthening effect is realized, but gas elements such as nitrogen and the like are extremely unfavorable for toughness of steel, so that the toughness of the steel is reduced while the strength and hardness of the steel are improved, the brittleness of the steel is increased, and macroscopic tissue looseness or air holes can be caused due to the fact that the nitrogen content is too high. Therefore, the iron element and other specific components are synergistic through specific proportioning relationship, so that the isotropy difference of the steel is small, the tissue distribution is more uniform, the performance difference of each place is small, and the steel has high strength and better extensibility.
Optionally, the mass percent of carbon comprises 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, and each value between such minimum and maximum values, or any two ranges of values.
The mass percentage of the silicon comprises 0.1%, 0.13%, 0.14%, 0.15%, 0.18%, 0.2%, 0.25%, and each value between the minimum value and the maximum value, or the range of any two values.
The mass percent of the manganese comprises 0.8%, 0.83%, 0.9, 1%, 1.2% and 1.3%, and each value between the minimum value and the maximum value or the range of any two values.
The mass percent of the vanadium comprises 0.01%, 0.015%, 0.02%, 0.025%, 0.03%, 0.035%, and each value between the minimum value and the maximum value, or the range of any two values.
The mass percentage of the titanium comprises 0.1%, 0.13%, 0.14%, 0.15%, and each value between the minimum value and the maximum value, or the range of any two values.
The mass percentage of the acid-soluble aluminum comprises 0.02%, 0.025%, 0.03%, 0.035%, 0.04%, 0.045%, 0.05%, 0.055%, 0.06%, and each value between the minimum value and the maximum value or the range of any two values.
The mass percent of the nitrogen comprises 0.001%, 0.002%, 0.0025%, 0.003%, 0.0035%, 0.004%, 0.0045%, 0.005%, 0.0055%, 0.006%, 0.007%, and each value between the minimum value and the maximum value, or a range of any two values.
It is understood that the unavoidable impurity elements are impurities which are inevitably carried in during the smelting process, limited by the raw materials or process conditions, and are present at levels known in the art that do not affect the properties of the alloy.
In some of these embodiments, the structure of the high strength steel includes ferrite, martensite, austenite, and cementite structures.
In some of these embodiments, the high strength steel is 1.2mm to 2mm thick.
In another aspect of the invention, a method for preparing high-strength steel is provided, which comprises the following steps S10-S30.
S10, providing preparation raw materials according to the above-mentioned metering ratio of the components of the high-strength steel, and sequentially carrying out smelting treatment and refining treatment on the preparation raw materials to prepare an alloy melt.
The preparation raw materials can be prepared according to the composition of the high-strength steel, the proportion of each element in the preparation raw materials can meet the composition of the high-strength steel, and the preparation raw materials have no special requirements on specific types and can be metal simple substances or alloys.
In some of these embodiments, before the step of performing the refining process, the following step S11 is further included:
and S11, carrying out ladle argon blowing treatment on the alloy melt prepared through smelting treatment.
In some of these embodiments, the temperature at the end of the argon station is controlled to be greater than 1542 ℃ during the step of the ladle argon blowing process.
In some embodiments, the refining process is performed at a temperature of 1570 ℃ to 1590 ℃ for a time of 40 minutes to 120 minutes.
Concretely, LF refining (ladle refining furnace) is adopted for refining treatment, wherein the LF tapping temperature is controlled to be 1570-1590 ℃.
After the refining treatment, the method further comprises the step of deep desulfurization of the refined molten steel in an LF furnace.
And S20, carrying out casting treatment, hot rolling treatment, cold rolling treatment and annealing treatment on the alloy melt in sequence to obtain the high-strength steel.
In some embodiments, the casting treatment adopts a continuous casting process, wherein the continuous casting pulling speed is controlled to be more than or equal to 3.8m/min, and the casting blank adopts a soft reduction mode.
In some of these embodiments, the hot rolling process includes the steps of:
And (3) heating the cast slab to ensure that the temperature of the slab is not less than 1180 ℃ and then rolling, wherein the initial rolling temperature is 1090-1150 ℃ and the final rolling temperature is 850-900 ℃, and the heating time is not less than 25min.
In some of these embodiments, after the step of hot rolling treatment and before the step of cold rolling treatment, the following step S21 is further included:
and S21, carrying out laminar cooling and acid washing treatment on the plate blank subjected to the hot rolling treatment in sequence. Specifically, after the plate blank is heated and subjected to hot rolling treatment by a 7-frame finishing mill group, the plate blank enters a laminar cooling system and is subjected to pickling treatment.
In some of these embodiments, the final cooling temperature of the laminar cooling is 590 ℃ to 640 ℃.
In some embodiments, the pickling process is performed at a speed of 30m/min to 120m/min to ensure that the surface is cleaned by pickling.
In some embodiments, the condition of the cold rolling treatment comprises controlling the single-pass reduction rate of a single stand to be more than or equal to 15 percent, and performing 3-5-pass reciprocating rolling at a rolling speed of 200-350 m/min.
In some embodiments, the annealing treatment conditions include performing a hydrogen blowing regime with a hood-type annealing furnace, and sequentially maintaining the temperature at 400 ℃, 520 ℃, 600 ℃ for 2 hours, and 10 hours, respectively.
In some of these embodiments, after the step of annealing, the method further comprises the steps of:
and flattening the annealed plate blank.
In some of these embodiments, the rolling force is controlled to 300±100 tons during the flattening process.
By controlling the rolling force of the flattening process, the plate shape is ensured to be tight.
In some of these embodiments, after the flattening step, the steel is oiled up in a timely manner to avoid rust.
In the preparation method, the conditions of each rolling step are further controlled, so that hardening measures such as solid solution strengthening, precipitation strengthening, dislocation strengthening, fine grain strengthening and the like are completed for each specific component, crystal grains with proper size are obtained by high-temperature deformation recrystallization of an austenite region, deformation of a low-temperature austenite unrecrystallized region and laminar cooling after rolling, stable and uniform strengthening tissues are obtained by annealing, and the performance of the steel is further improved.
The invention further provides the high-strength steel or the application of the high-strength steel prepared by the preparation method of the high-strength steel in preparation of automobile parts.
In still another embodiment of the present invention, there is provided a slide rail for an automobile, the slide rail comprising the high-strength steel described above or the high-strength steel produced by the method for producing the high-strength steel described above.
The steel has small isotropy difference, more uniform tissue distribution, small performance difference at all parts, high strength and better elongation, small thickness tolerance when being manufactured into a steel plate, high control precision, and the thickness precision can reach +/-20 mu m when the target thickness is less than or equal to 2mm.
The invention will be described in connection with specific embodiments, but the invention is not limited thereto, and it will be appreciated that the appended claims outline the scope of the invention, and those skilled in the art, guided by the inventive concept, will appreciate that certain changes made to the embodiments of the invention will be covered by the spirit and scope of the appended claims.
Specific examples the following are specific examples.
Example 1
(1) The mass percentages of the elements of the high-strength steel are shown in the table 1, and corresponding preparation raw materials are provided.
(2) The method comprises the steps of smelting raw materials into molten iron through a 100-ton converter, blowing argon into a ladle, controlling the temperature of an end point of an argon station to be higher than 1542 ℃ in the step of blowing argon into the ladle, then transferring the molten iron into an LF furnace for refining, wherein the refining temperature is 1570-1590 ℃ and the time is 40 minutes, carrying out deep desulfurization on the molten steel in the LF furnace, then carrying out continuous casting, controlling the continuous casting drawing speed to be 3.8m/min, and obtaining a slab with the thickness of 70mm by adopting a light-pressure mode.
(3) Heating the slab to 1192 ℃ for 31min, performing thermo-mechanical controlled rolling by a 7-frame continuous rolling unit, wherein the initial rolling temperature is 1134 ℃, cooling the steel strip by ACC control cooling after rolling, the coiling temperature is 606 ℃, the thickness specification of the hot rolled coil is 2.028mm, then uncoiling the hot rolled steel coil, pickling at 86m/min speed, and the acid liquor concentration is 62g/L, 112g/L and 161g/L respectively, then performing cold rolling by a single frame, namely 3 times rolling to obtain a steel coil with the thickness of 1.68mm, and then performing cover annealing, namely performing hydrogen blowing system by a cover annealing furnace, sequentially performing heat preservation at 400 ℃, 520 ℃ and 600 ℃ for 2 hours, 2 hours and 10 hours respectively, discharging the steel coil at 82 ℃ after cooling, and finally performing leveling treatment by using leveling rolling force of 312 tons to obtain the high-strength steel coil.
(4) And respectively sampling the high-strength steel coil prepared by the steps, and placing the surface layer, the section with the thickness of 1/4 and the section with the thickness of 1/2 of the high-strength steel coil under an electron microscope image to observe metallographic structures, wherein the metallographic structures are respectively shown in figures 1-3, and the uniformity of the structures of the steel everywhere is high.
(5) The positions of the coil head force, the coil middle force and the coil tail force of the high-strength steel coil prepared by the steps are respectively sampled, namely, the head longitudinal direction, the head transverse direction, the tail longitudinal direction, the tail transverse direction, the middle longitudinal direction and the middle transverse direction are respectively subjected to sampling marks, and the mechanical property test is respectively carried out by adopting an industry standard test, and the results are shown in a table 2.
The test results show that the steel prepared by the steps has high strength, good elongation and good performance uniformity, the fluctuation of the strength of the head and the tail is within 25Mpa, the yield strength of the obtained steel plate is over 900Mpa, the tensile strength is also greater than 900Mpa, the elongation is more than or equal to 12%, and the yield ratio is close to 1.
Examples 2 to 3
Examples 2 to 3 are substantially the same as example 1, except that the mass percentage of each element in the high strength steel in step (1) is different from that in example 1, and the specific reference is given in Table 1.
The other steps and conditions are the same as those of example 1, and the mechanical property test results of examples 2 to 3 are shown in tables 3 and 4, respectively.
The compositions of the high-strength steels of examples 1 to 3 are shown in Table 1.
TABLE 1
| Content (%) | C | Si | Mn | P | S | Als | V | Ti | N | Fe |
| Example 1 | 0.055 | 0.16 | 1.04 | 0.012 | 0.0026 | 0.029 | 0.022 | 0.119 | 0.0035 | Allowance of |
| Example 2 | 0.061 | 0.17 | 1.1 | 0.011 | 0.003 | 0.035 | 0.027 | 0.13 | 0.0043 | Allowance of |
| Example 3 | 0.071 | 0.13 | 1.11 | 0.015 | 0.0021 | 0.031 | 0.02 | 0.114 | 0.0045 | Allowance of |
The results of the mechanical properties of high strength obtained in example 1 are shown in Table 2.
TABLE 2
The results of the mechanical properties of high strength obtained in example 2 are shown in Table 3.
TABLE 3 Table 3
The results of the mechanical properties of high strength obtained in example 3 are shown in Table 4.
TABLE 4 Table 4
As is clear from the data in tables 2-4, the high-strength steel material has the advantages of small isotropy difference, more uniform tissue distribution, small performance difference at each place and high strength and better elongation.
The technical features of the above-described embodiments may be arbitrarily combined, and all possible combinations of the technical features in the above-described embodiments are not described for brevity of description, however, as long as there is no contradiction between the combinations of the technical features, they should be considered as the scope of the description.
The above examples illustrate only a few embodiments of the invention, which are described in detail and are not to be construed as limiting the scope of the invention. It should be noted that it will be apparent to those skilled in the art that several variations and modifications can be made without departing from the spirit of the invention, which are all within the scope of the invention. Accordingly, the scope of protection of the present invention is to be determined by the appended claims.
Claims (10)
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