CN111218607A - A kind of high-strength seat slide rail steel and its production method based on thin strip casting and rolling - Google Patents
A kind of high-strength seat slide rail steel and its production method based on thin strip casting and rolling Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 122
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- 238000005096 rolling process Methods 0.000 title claims abstract description 60
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 44
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- 238000000034 method Methods 0.000 claims abstract description 35
- 238000005098 hot rolling Methods 0.000 claims abstract description 19
- 238000001816 cooling Methods 0.000 claims abstract description 17
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- 229910052758 niobium Inorganic materials 0.000 claims abstract description 13
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 13
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 9
- 239000000443 aerosol Substances 0.000 claims abstract description 5
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- 238000009628 steelmaking Methods 0.000 claims description 7
- 238000003723 Smelting Methods 0.000 claims description 6
- 238000009749 continuous casting Methods 0.000 claims description 6
- 238000005261 decarburization Methods 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 5
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- 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
- B21B1/463—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a continuous process, i.e. the cast not being cut before rolling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/58—Roll-force control; Roll-gap control
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- 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
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
- C21D8/0215—Rapid solidification; Thin strip casting
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- 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
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- 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
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- 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
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B2015/0057—Coiling the rolled product
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- 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
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Abstract
本发明属于钢铁生产技术领域，特别涉及一种高强度座椅滑轨用钢及其基于薄带铸轧生产的方法。钢水经薄带连铸获得铸带，铸带经单道次热轧、气雾冷却后卷取获得热轧卷，随后热轧卷在连续退火酸洗线上打开，经退火段、酸洗段后清洗涂油卷取获得高强酸洗卷。本发明采用薄带铸轧+连续退火酸洗工艺生产高强座椅滑轨用钢，解决了传统热轧工艺难以生产薄规格高强度、高尺寸精度产品的问题，以及热轧+酸洗+冷轧+退火工艺流程长、能耗高、产品各向同性差的问题。本发明产品采用低温卷取获得高屈强比的棒状贝氏体相，后续退火工艺使Nb、V等充分析出，相变应力释放，在实现高强度、高屈强比的同时，进一步提升塑性，更适宜制造座椅滑轨。
The invention belongs to the technical field of iron and steel production, and particularly relates to a high-strength seat slide rail steel and a method for producing it based on thin strip casting and rolling. The molten steel is continuously cast through thin strips to obtain cast strips, and the cast strips are subjected to single-pass hot rolling and aerosol cooling to obtain hot-rolled coils. After cleaning and oiling the coils, high-strength pickling coils are obtained. The invention adopts the thin strip casting and rolling + continuous annealing and pickling process to produce high-strength seat slide rail steel, which solves the problem that the traditional hot-rolling process is difficult to produce thin-gauge, high-strength and high-dimensional precision products, as well as hot rolling + pickling + cooling The problems of long rolling + annealing process, high energy consumption and poor product isotropy. The product of the invention adopts low-temperature coiling to obtain a rod-shaped bainite phase with a high yield-strength ratio, and the subsequent annealing process makes Nb, V, etc. fully decomposed, and the phase transformation stress is released. While achieving high strength and high yield-strength ratio, the plasticity is further improved. , more suitable for the manufacture of seat slides.
Description
Technical Field
The invention belongs to the technical field of steel production, and particularly relates to high-strength seat slide rail steel and a method for producing the same based on thin-strip casting and rolling.
Background
In recent years, in the field of automobiles, high-strength thin steel plates are applied to structural members, safety parts and the like of automobile body frameworks, so that the light weight, energy conservation and consumption reduction are promoted, and remarkable economic and social benefits are generated. The quality and safety of the automobile seat as a part for connecting a passenger and an automobile body are important indexes for measuring the performance of the automobile. The front and back adjustment of the seat is completed by a slide rail assembly arranged below the seat, the quality of the seat slide rail is directly related to the safety of a driver, and the seat slide rail has very strict safety indexes, large processing difficulty and high technical requirement, and is one of the most complex components with the quality requirement in seat parts.
Firstly, the seat slide rail has high requirements on the mechanical properties of raw steel. The high-strength high-yield-ratio material is selected because the deformation is not allowed during the service process, and the high-strength high-yield-ratio material has good rigidity and deformation resistance. When the automobile seat slide rail is produced, high-speed punch forming is adopted, and if large-size inclusions or precipitates exist in steel, cracking is easily caused during processing. Particularly, when Ti is added into molten steel, coarse Ti-containing carbonitride particles are precipitated in the solidification process, the coarse particles are easy to crack during high-speed stamping, the forming performance of the material is influenced, and potential safety hazards exist in the use process, so that the requirement of the seat slide rail material on the Ti content is strict. In order to ensure the precision of the parts after stamping forming, the head, middle and tail mechanical properties of the rolled steel raw material are required to be uniform, the properties in the longitudinal direction, the transverse direction and the 45-degree direction are relatively consistent, and obvious anisotropy cannot occur. In addition, the slide rail manufacturing belongs to the precision manufacturing industry, and in order to avoid the functional failure phenomena such as jamming or difficult control when the slide rail is subjected to positive pressure and side pulling, the slide rail has a stricter requirement on the thickness precision of the raw material steel plate compared with the general stamping parts on the automobile.
In view of the above requirements, the steel plate used for manufacturing the slide rail material is required to have high strength, high yield ratio, high plasticity and formability, good performance uniformity and isotropy, and high requirement on thickness precision, so that the production difficulty of the steel for the seat slide rail is very high. The product performance and the dimensional accuracy of the conventional hot continuous rolling production line are difficult to realize at present, and the cold-rolled high-strength steel produced by adopting the hot rolling, pickling, cold rolling and annealing process has the problems of long production flow, multiple working procedures, high energy consumption, large environmental load and the like, and the cost is relatively high.
The thin strip casting and rolling is a novel thin strip production method, which is a short-flow near-net-shape processing technology integrating rapid solidification and rolling deformation, and compared with the traditional hot continuous rolling technology, the method omits the working procedures of a heating furnace, multi-pass rough rolling and the like, simplifies multi-frame finish rolling into only one frame, and greatly shortens the process flow.
In order to provide a product with better performance, reduce the production flow, realize energy conservation and environmental protection and reduce the production cost, the invention provides a method for manufacturing high-strength seat sliding rail steel based on thin strip casting and rolling.
Disclosure of Invention
In view of the above problems, the invention provides a method for manufacturing a high-strength steel for seat sliding rails based on thin-strip casting and rolling, which aims to solve the problems that the product performance and the dimensional accuracy of the conventional hot continuous rolling production line are difficult to realize, and the cold-rolled high-strength steel produced by adopting the hot rolling, pickling, cold rolling and annealing processes has the disadvantages of long production flow, multiple processes, high energy consumption, large environmental load and the like, so that the production cost is reduced, and the material performance is more suitable for manufacturing the seat sliding rails.
In order to achieve the purpose, the invention adopts the following technical scheme.
According to an aspect of the present invention, there is provided a method for producing a high strength seat rail steel based on thin strip casting, comprising the steps of:
(1) smelting to obtain molten steel, wherein the molten steel is prepared from the following chemical components in percentage by mass: c: 0.01-0.05%, Mn: 0.8-1.6%, Si: 0.1-0.5%, Cr: 0.1-0.4%, Nb: 0.04-0.08%, V: 0.02 to 0.06%, Al: less than or equal to 0.003 percent, P: less than or equal to 0.02 percent, S: less than or equal to 0.005 percent, and the balance of Fe and inevitable impurity elements;
(2) continuously casting the molten steel obtained in the step (1) into a thin strip to obtain a cast strip;
(3) hot rolling the cast strip obtained in the step (2) into a thin strip for one time, wherein the reduction rate of the hot rolling is 10-40%, and the outlet temperature is 780-950 ℃;
(4) cooling the thin strip obtained in the step (3) to 450-;
(5) uncoiling the hot rolled coil obtained in the step (4) on a continuous annealing pickling line, wherein the temperature of a soaking section of an annealing furnace is 600-720 ℃;
(6) and (4) the strip steel enters an acid washing section after being discharged from the annealing furnace, and is oiled, coiled and packaged after acid washing.
According to the method for producing the high-strength seat sliding rail steel based on the thin strip casting rolling, the converter steel making or the electric furnace steel making, the VD vacuum decarburization and deoxidation and the LF refining are preferably adopted, and molten steel with qualified components is obtained.
According to the method for producing the steel for the high-strength seat slide rail based on the strip casting, according to the present invention, preferably, in the step (2), the molten steel is cast-rolled using a twin roll strip casting apparatus at a casting speed of 35 to 100m/min under the protection of inert gas.
According to the method for producing the steel for a high strength seat rail based on thin strip casting, according to the present invention, preferably, in the step (2), the thickness of the cast strip is 1.5 to 2.5 mm.
According to the method for producing the steel for a high strength seat slide rail based on strip casting, according to the present invention, preferably, in the step (3), the thickness of the strip is 1.2 to 2.0 mm.
According to the method for producing the high-strength seat rail steel based on strip casting, provided by the invention, in the step (4), the matrix structure obtained by low-temperature coiling is preferably fine short rod bainite.
According to the method for producing the steel for high strength seat rails based on thin strip casting, according to the present invention, preferably, in the step (5), the heating time of the steel strip in the annealing furnace is 2 to 10 min.
According to another aspect of the present invention, there is provided a high strength seat rail steel produced using the method having any combination of the aforementioned features.
According to the high-strength seat rail steel of the present invention, the microstructure of the high-strength seat rail steel is preferably precipitated particles containing Nb and V uniformly distributed on a fine rod-like bainite matrix.
According to the high strength seat track steel of the present invention, preferably, the obtained hot-rolled thin strip steel has a yield strength of 780MPa or more, a tensile strength of 850MPa or more, an elongation of 12% or more, and a yield ratio of 0.90 or more.
According to the high-strength seat slide rail steel, the material coil is preferably uniform in head-to-tail performance, and the strength difference is within +/-15 MPa; good isotropy, and the strength difference in the transverse direction, the longitudinal direction and the 45-degree direction is within +/-15 MPa.
According to the high strength seat rail steel of the present invention, it is preferable that the thickness tolerance of the high strength seat rail steel is controlled within ± 25 μm.
The excellent mechanical properties, thickness tolerance and the like also benefit from the following technical advantages of the thin strip casting process in producing the high-strength seat slide steel to a great extent.
In the strip casting and rolling process, the time from the solidification of molten steel into strip steel to the coiling is about 20 seconds, and the short time causes insufficient time for the added Nb and V to be precipitated. Meanwhile, the driving force for precipitation is insufficient due to the small total rolling reduction. Therefore, under the strip casting and rolling process, most of elements such as Nb, V and the like still exist in a solid solution form in the matrix after coiling, and the solid solution form is different from the precipitation form in the traditional hot rolled product. In the subsequent annealing process, a large amount of solid-dissolved elements such as Nb and V begin to be separated out, and fine precipitates can be realized by controlling the annealing temperature, so that on one hand, the strength is obviously improved, meanwhile, the small precipitates cannot obviously influence the plasticity, and the plasticity is also improved due to the release of the phase change stress.
The hot rolled coil produced by the thin strip casting and rolling process is coiled at low temperature to obtain a matrix phase with high yield ratio, then annealing treatment is carried out to ensure that Nb and V which are not precipitated in the thin strip casting and rolling product are continuously precipitated to show obvious strengthening effect, and phase change stress is released at the same time to ensure that the strength and the plasticity of the material are simultaneously improved, the high yield ratio is realized while the high strength and the good plasticity are realized, and the method is very suitable for producing seat slide rails.
The casting and rolling process of the thin strip belongs to complete endless rolling, and the head, the middle and the tail of the produced steel coils have no performance difference. In addition, the cast strip is thin, the rolling reduction of a single stand is small, the transverse and longitudinal properties of the steel plate are basically not different, and the isotropy is good. In addition, compared with the traditional hot rolling production line, the single-rack rolling of the thin strip casting and rolling production line has obvious advantages in the control precision of the thickness of the steel plate, and the thickness precision of products with the thickness specification of 1.0-2.0mm can be controlled within +/-10 mu m in a high-precision control mode.
Advantageous technical effects
Compared with the prior art, the invention has the characteristics and beneficial technical effects that:
① the high-strength seat sliding rail steel based on thin strip casting and rolling is produced by adopting the thin strip casting and rolling and continuous annealing and pickling processes, compared with the traditional hot continuous rolling and hot rolling, pickling, cold rolling and annealing processes, the production process is obviously reduced, the energy consumption and emission are less, and the production cost and the labor cost are greatly reduced.
② the high strength seat sliding rail steel based on the thin strip casting and rolling adopts low temperature coiling to obtain the rod-shaped bainite matrix phase with high strength and high yield ratio, and Nb and V still exist in a solid solution state, and then Nb and V-containing particles with strong strengthening effect are precipitated during annealing, so that the strength is improved, phase change stress is released, the plasticity is further improved, and finally high strength and high yield ratio are realized, and good plasticity is realized.
③ the high strength seat sliding rail steel based on thin strip casting rolling of the invention, the produced steel coil has small difference of the head, middle and tail performance, good performance uniformity, in addition, because the rolling reduction of single stand is relatively small, the transverse and longitudinal performance of the steel plate has no difference basically, the isotropy is good.
④ the steel for high-strength seat sliding rail based on thin strip casting and rolling has small tolerance of steel plate thickness, high control precision, controllable product thickness precision within +/-25 μm, controllable within +/-10 μm under high-precision control mode, equivalent to cold rolled product, and far better than traditional hot rolled product.
In conclusion, the high-strength seat sliding rail steel based on thin-strip casting and rolling has the advantages of short production process, environmental friendliness and the like, and is low in production cost. The product has high strength, high yield ratio, high plasticity, good performance uniformity and isotropy, high requirement on thickness precision and natural advantage when being used for manufacturing the automobile seat slide rail.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings of the embodiments will be briefly described below. It is to be understood that the drawings in the following description are directed to only some embodiments of the invention and are not intended as a limitation on the invention.
FIG. 1 is a flow chart of a production process according to an embodiment of the present invention.
FIG. 2 is an exemplary fluctuation curve of the thickness of a steel coil for a high strength seat rail produced according to an embodiment of the present invention.
Fig. 3 is a metallographic structure of steel for a high-strength seat rail produced according to example 1 of the present invention.
Fig. 4 shows fine precipitated particles uniformly distributed in the structure of the high strength seat rail steel produced according to example 1 of the present invention.
Fig. 5 is a metallographic structure of steel for a high-strength seat rail produced according to example 2 of the present invention.
Fig. 6 shows fine precipitated particles uniformly distributed in the structure of the high strength seat rail steel produced according to example 2 of the present invention.
Fig. 7 is a metallographic structure of steel for a high-strength seat rail produced according to example 3 of the present invention.
Fig. 8 shows fine precipitated particles uniformly distributed in the structure of the high strength seat rail steel produced according to example 3 of the present invention.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions of the embodiments of the present invention will be clearly and completely described below. It is to be understood that the embodiments described are only a few embodiments of the present invention, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the described embodiments of the invention without any inventive step, are within the scope of protection of the invention.
Unless defined otherwise, technical or scientific terms used herein shall have the ordinary meaning as understood by one of ordinary skill in the art to which this invention belongs.
A schematic of the overall process flow employed by an embodiment of the present invention is shown, for example, in fig. 1.
Referring to fig. 1, in various embodiments, the method for producing a high strength seat rail steel based on thin strip casting according to the present invention mainly includes the process steps of: smelting, thin strip continuous casting, hot rolling, aerial fog cooling, coiling, uncoiling, annealing, acid washing, cleaning, oiling, coiling, packaging and the like.
Further, FIG. 2 is an exemplary fluctuation curve of thickness of a steel coil for a high strength seat rail produced according to various embodiments of the present invention, wherein the thickness unit mm on the vertical axis and the length unit m on the horizontal axis.
Referring to fig. 2, the high strength steel for seat rails according to the embodiments of the present invention has a small tolerance of steel plate thickness, a high control precision, a thickness precision of a product controlled within ± 25 μm, and a high precision control mode controlled within ± 10 μm, which is equivalent to a cold rolled product and much better than a conventional hot rolled product.
Details of examples 1-3 according to the present invention are further detailed below.
Example 1
(1) Smelting: in the step (1), electric furnace steelmaking, VD vacuum decarburization and deoxidation and LF refining are adopted to obtain molten steel with qualified components.
Wherein the molten steel comprises the following components in percentage by weight: c: 0.030, Mn: 1.45, Si: 0.37, Cr: 0.28, Nb: 0.068, V: 0.032, P: 0.012, S: 0.002, Al: 0.002, and the balance of Fe and impurity elements.
(2) Strip continuous casting: and (3) casting and rolling the molten steel with qualified components by adopting thin strip casting and rolling equipment, wherein an exemplary casting and rolling speed is 67m/min under the protection of inert gas, and a cast strip with the thickness of 1.85mm is obtained.
(3) Hot rolling: the cast strip was rolled into a 1.47mm thin strip by a single hot rolling pass at a reduction of 21% and a mill exit temperature of 825 ℃.
(4) Cooling and coiling: and cooling the hot-rolled thin strip by an aerosol cooling system, then coiling at 435 ℃, and then cooling to room temperature in air to obtain a hot-rolled coil.
(5) Annealing: and (3) after the hot rolled coil is uncoiled, feeding the hot rolled coil into an annealing furnace, controlling the temperature of a soaking section of the annealing furnace to be 650 ℃, and controlling the strip speed to enable the strip steel to stay for 6min in the soaking section.
(6) Acid washing: the strip steel passes through the annealing furnace and then enters the pickling section through a loop, and the temperature of the acid liquor is 79 ℃. And then the mixture is oiled, coiled and packaged after passing through a cleaning section.
Table 1 shows the mechanical properties in the transverse, rolling and 45 ° directions of the steel sheet obtained according to the method of example 1.
As can be seen from table 1, the steel for a high strength seat rail according to example 1 of the present invention is good in performance uniformity. Wherein the yield strength of the obtained hot-rolled thin strip steel is more than 780MPa, the tensile strength is more than 850MPa, the total elongation is more than 12 percent, and the yield ratio is more than 0.90.
In addition, referring also to table 1, since the rolling reduction of the single stand rolling is relatively small, there is substantially no difference in transverse and longitudinal properties of the steel sheet, and the isotropy is good. Specifically, the material roll has uniform head-to-tail performance and the strength difference is within +/-15 MPa. Referring to Table 1, the isotropy is good, and the strength difference in the transverse direction, the longitudinal direction and the 45-degree direction is within +/-15 MPa.
Fig. 3 is a metallographic structure of steel for a high-strength seat rail produced according to example 1 of the present invention. Further, fig. 4 shows fine precipitated particles uniformly distributed in the steel structure for a high strength seat rail produced according to example 1 of the present invention.
As can be seen from fig. 3, the high strength seat rail steel produced according to example 1 of the present invention, the strip casting rolling, which uses low temperature coiling to obtain a fine rod-shaped bainite matrix phase having high strength, is not changed in phase upon annealing.
As shown in fig. 4, the high strength steel for seat rails produced according to example 1 of the present invention precipitates Nb and V-containing precipitated particles having a strong strengthening effect during annealing aging, and the strength of the final structure is further improved compared to that in a hot rolled state, thereby achieving high strength and high yield ratio, and also achieving good plasticity by releasing the transformation stress through annealing.
Example 2
(1) Smelting: in the step (1), electric furnace steelmaking, VD vacuum decarburization and deoxidation and LF refining are adopted to obtain molten steel with qualified components. The weight percentages are as follows: c: 0.026, Mn: 1.37, Si: 0.42, Cr: 0.22, Nb: 0.074, V: 0.038, P: 0.015, S: 0.003, Al: 0.003, and the balance of Fe and impurity elements.
(2) Strip continuous casting: and (3) casting and rolling the molten steel with qualified components by adopting thin strip casting and rolling equipment, wherein the casting and rolling speed is 62m/min under the protection of inert gas, and a cast strip with the thickness of 1.96mm is obtained.
(3) Hot rolling: the cast strip is rolled into a thin strip with the thickness of 1.58mm by one-time hot rolling with the rolling reduction of 19 percent, and the outlet temperature of the rolling mill is 808 ℃.
(4) Cooling and coiling: and cooling the hot-rolled thin strip by an aerosol cooling system, then coiling at 410 ℃, and then cooling to room temperature in an air manner to obtain a hot-rolled coil.
(5) Annealing: and (3) after the hot rolled coil is uncoiled, feeding the hot rolled coil into an annealing furnace, controlling the temperature of a soaking section of the annealing furnace to be 673 ℃, and controlling the strip speed to enable the strip steel to stay for 5min in the soaking section.
(6) Acid washing: the strip steel passes through the annealing furnace and then enters the pickling section through a loop, and the temperature of the acid liquor is 78 ℃. And then the mixture is oiled, coiled and packaged after passing through a cleaning section.
Table 2 shows the mechanical properties in the transverse, rolling and 45 ° directions of the steel sheet obtained according to the method of example 2.
As can be seen from table 2, the steel for a high strength seat rail according to example 2 of the present invention is good in performance uniformity. Wherein the yield strength of the obtained hot-rolled thin strip steel is more than 780MPa, the tensile strength is more than 850MPa, the total elongation is more than 12 percent, and the yield ratio is more than 0.90.
In addition, referring also to table 2, since the rolling reduction of the single stand rolling is relatively small, there is substantially no difference in transverse and longitudinal properties of the steel sheet, and the isotropy is good. Specifically, the material roll has uniform head-to-tail performance and the strength difference is within +/-15 MPa.
Fig. 5 is a metallographic structure of steel for a high-strength seat rail produced according to example 2 of the present invention. Further, fig. 6 shows fine precipitated particles uniformly distributed in the steel structure for a high strength seat rail produced according to example 2 of the present invention.
As can be seen from fig. 5, the high strength seat rail steel produced according to example 2 of the present invention, the strip casting rolling, which uses low temperature coiling to obtain a fine rod-shaped bainite matrix phase having high strength, is not changed in phase upon annealing.
As shown in fig. 6, the high strength steel for seat rails produced according to example 2 of the present invention precipitates Nb and V-containing precipitated particles having a strong strengthening effect during annealing aging, and the strength of the final structure is further improved compared to that in a hot rolled state, thereby achieving high strength and high yield ratio, and also achieving good plasticity by releasing the transformation stress through annealing.
Example 3
(1) Smelting: in the step (1), converter steelmaking, VD vacuum decarburization and deoxidation and LF refining are adopted to obtain molten steel with qualified components. The weight percentages are as follows: c: 0.037, Mn: 1.58, Si: 0.35, Cr: 0.20, Nb: 0.056, V: 0.045, P: 0.011, S: 0.003, Al: 0.002, and the balance of Fe and impurity elements.
(2) Strip continuous casting: and (3) casting and rolling the molten steel with qualified components by adopting thin strip casting and rolling equipment, wherein the casting and rolling speed is 59m/min under the protection of inert gas, and a casting strip with the thickness of 2.02mm is obtained.
(3) Hot rolling: the cast strip was rolled into a 1.72mm thin strip by a single hot rolling pass at 15% reduction, the exit temperature of the mill being 848 ℃.
(4) Cooling and coiling: and cooling the hot-rolled thin strip by an aerosol cooling system, then coiling at 396 ℃, and then cooling to room temperature in an air manner to obtain a hot-rolled coil.
(5) Annealing: and (3) after the hot rolled coil is uncoiled, feeding the hot rolled coil into an annealing furnace, controlling the temperature of a soaking section of the annealing furnace to be 640 ℃, and controlling the strip speed to enable the strip steel to stay for 8min in the soaking section.
(6) Acid washing: the strip steel passes through the annealing furnace and then enters the pickling section through a loop, and the temperature of the acid liquor is 80 ℃. And then the mixture is oiled, coiled and packaged after passing through a cleaning section.
Table 3 shows the mechanical properties in the transverse, rolling and 45 ° directions of the steel sheet obtained according to the method of example 3.
As can be seen from table 3, the high strength seat rail steel according to example 3 of the present invention is good in performance uniformity. Wherein the yield strength of the obtained hot-rolled thin strip steel is more than 780MPa, the tensile strength is more than 850MPa, the total elongation is more than 12 percent, and the yield ratio is more than 0.90.
In addition, referring also to table 3, since the rolling reduction of the single stand rolling is relatively small, there is substantially no difference in transverse and longitudinal properties of the steel sheet, and the isotropy is good. Specifically, the material roll has uniform head-to-tail performance and the strength difference is within +/-15 MPa.
Fig. 7 is a metallographic structure of steel for a high-strength seat rail produced according to example 3 of the present invention. Further, fig. 8 shows fine precipitated particles uniformly distributed in the steel structure for a high strength seat rail produced according to example 3 of the present invention.
As can be seen from fig. 7, the high strength seat rail steel produced according to example 3 of the present invention, the strip casting rolling, which uses low temperature coiling to obtain a fine rod-shaped bainite matrix phase having high strength, is not changed in phase upon annealing.
As shown in fig. 8, the high strength steel for seat rails produced according to example 3 of the present invention precipitates Nb and V-containing precipitated particles having a strong strengthening effect during annealing aging, and the strength of the final structure is further improved compared to that in a hot rolled state, thereby achieving high strength and high yield ratio, and also achieving good plasticity by releasing the transformation stress through annealing.
In summary, the high-strength steel for seat rails produced according to the embodiment of the invention is produced by adopting the processes of thin-strip casting and rolling and continuous annealing and pickling based on the thin-strip casting and rolling process, and compared with the conventional processes of hot continuous rolling and hot rolling, pickling, cold rolling and annealing, the production process is obviously reduced, the energy consumption and emission are less, and the production cost and the labor cost are greatly reduced. The high-strength seat slide rail steel produced according to the embodiment of the invention has the advantages of short production process, environmental protection and the like, and is low in production cost. The product has high strength, high yield ratio, high plasticity, good performance uniformity and isotropy, high requirement on thickness precision and natural advantage when being used for manufacturing the automobile seat slide rail.
The foregoing is directed to embodiments of the present invention and it is noted that various modifications and adaptations of the invention may occur to those skilled in the art without departing from the scope and spirit of the invention.
Claims (12)
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| CN113430466A (en) * | 2021-06-24 | 2021-09-24 | 江苏沙钢集团有限公司 | Ultrahigh-strength steel for lower bottom plate of new energy automobile battery pack and production method thereof |
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