CN114058949B - Hot-forming steel pickling plate and method for reducing intercrystalline oxidation of surface of steel pickling plate - Google Patents
Hot-forming steel pickling plate and method for reducing intercrystalline oxidation of surface of steel pickling plate Download PDFInfo
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- CN114058949B CN114058949B CN202111212641.XA CN202111212641A CN114058949B CN 114058949 B CN114058949 B CN 114058949B CN 202111212641 A CN202111212641 A CN 202111212641A CN 114058949 B CN114058949 B CN 114058949B
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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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- 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
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the 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
- 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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- 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
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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
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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
- C22C38/26—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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
- C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
- C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
- C23G1/08—Iron or steel
Abstract
The invention relates to the technical field of steel rolling, in particular to a hot-formed steel pickling plate and a method for reducing intercrystalline oxidation on the surface of the hot-formed steel pickling plate. The chemical components of the hot-formed acid-pickled steel plate comprise the following components in percentage by mass: c:0.2-0.3%, si:0.15-0.25%, mn:1-1.5%, cr:0.1-0.3%, nb:0.02 to 0.04%, sb:0.03-0.1%, the balance being Fe and unavoidable impurity elements; the control is mainly characterized in that the control and the matching of Si element in steel grade are related processes, such as heating temperature and time; solves the problem of intergranular oxidation of the surface of the hot-formed steel pickling plate, and can improve the surface quality and the formability of the pickling plate.
Description
Technical Field
The invention relates to the technical field of steel rolling, in particular to a hot-formed steel pickling plate and a method for reducing intercrystalline oxidation on the surface of the hot-formed steel pickling plate.
Background
The hot-rolled pickled plate is a product between a cold-rolled plate and a hot-rolled plate, but the quality requirement is higher than that of the hot-rolled plate, and part of the hot-rolled pickled plate needs to be produced according to the quality requirement of the cold-rolled plate. In practical production, the hot-rolled pickled steel plate has surface quality defects such as pits, oxygen spots, scratches, waist folds, under-pickling, over-pickling and the like, and the main reason is intergranular oxidation.
The trembling research finds that the intercrystalline oxidation is more serious when the high-carbon chromium stainless steel 440C is quenched in an air furnace, the intercrystalline oxidation is aggravated when the quenching temperature is increased or the heat preservation time is prolonged, and the intercrystalline oxidation is more sensitive to the heat preservation time. The researches on the Zhao modest and the like find that the intergranular oxidation behavior of Fe-36Ni Invar alloys with different total oxygen contents is that the higher the oxidation temperature is, the faster the reaction substances are diffused, the larger the thickness of the intergranular oxidation layer is, the more serious the oxidation is, and when the total oxygen content in the steel is higher, the reaction substances are favorable for being diffused along the grain boundary, so that the more serious intergranular oxidation phenomenon is caused. Van YongFei and other researches on the band-shaped cracks on the edge of the hot-rolled high manganese steel plate find that the high carbon high manganese steel is a steel type which is easy to be selectively oxidized, the naked columnar crystal boundary in the heating process is a channel for oxygen atom diffusion, and developed columnar crystals are easy to be oxidized, which is a main reason for generating cracks on the hot-rolled high manganese steel plate. However, the research does not relate to the generation mechanism and control measure of the intergranular oxidation in the hot rolling process of the steel products.
The generation of intergranular oxidation causes surface cracking easily to occur in the stamping process of the acid-washing plate steel, and meanwhile, the more serious intergranular oxidation also causes defects such as color difference or corrosion and the like after acid washing.
Disclosure of Invention
The application provides a hot-formed steel pickled plate and a method for reducing surface intercrystalline oxidation of the hot-formed steel pickled plate, which aim to solve the technical problem that intercrystalline oxidation is easy on the surface of pickled plate steel in the prior art.
In a first aspect, the present application provides a thermoformed pickled steel sheet having a chemical composition, in mass fractions, comprising: c:0.2-0.3%, si:0.15-0.25%, mn:1-1.5%, cr:0.1-0.3%, nb:0.02 to 0.04%, sb:0.03-0.1%, and the balance of Fe and inevitable impurity elements.
Optionally, the metallographic structure of the hot-formed pickled steel plate comprises, by volume fraction: 10% -20% of ferrite and 80-90% of pearlite.
Optionally, in the austenite, the austenite element diffusion coefficient at 850 ℃ is: DO- γ =2.47 × 10 -12 ，DSi-γ＝4.06×10 -17 ，DMn-γ＝1.04×10 -17 (ii) a In the ferrite, the diffusion coefficient of ferrite elements at 850 ℃ is as follows: DO- α =2.00 × 10 -11 ；DSi-α＝4.27×10 -15 ；DMn-α＝2.74×10 -15 。
In a second aspect, the present application provides a method of reducing intergranular oxidation of the surface of a pickled hot formed steel sheet, the method comprising the steps of:
obtaining a casting blank containing the chemical components;
measuring and obtaining the nose tip temperature of an intergranular oxidation depth curve of the casting blank;
controlling a finish rolling process according to the nose tip temperature;
sequentially carrying out multi-section heating, rough rolling and finish rolling on the casting blank to obtain a rolled casting blank;
calculating and obtaining the austenite element diffusion coefficient and the ferrite element diffusion coefficient of the hot-formed steel pickling plate at a certain temperature;
carrying out layer cooling and coiling on the rolled casting blank according to the austenite element diffusion coefficient and the ferrite element diffusion coefficient of the hot-formed steel pickling plate to obtain a hot-rolled coil;
and uncoiling and pickling the hot-rolled coil in sequence to obtain the hot-formed steel pickled plate.
Optionally, the step of controlling the finish rolling process according to the nose tip temperature comprises:
the nose tip temperature is 750 ℃, the nose tip temperature interval is 700-800 ℃, the nose tip temperature interval is avoided in the finish rolling process, and the influence of low-temperature intergranular oxidation in finish rolling is controlled: the initial rolling temperature of the finish rolling is 1040-1080 ℃, the rolling speed of the finish rolling is controlled to be 8m/s, and the actual final rolling temperature is 880-900 ℃.
Optionally, the step of performing layer cooling and coiling on the rolled casting blank according to the austenite element diffusion coefficient and the ferrite element diffusion coefficient of the hot-formed steel-pickled plate comprises:
determining diffusion coefficients of Si, mn and O elements in ferrite and in austenite, determining a ferrite temperature interval and an austenite temperature interval, regulating the ferrite temperature interval and the austenite temperature interval in the layer cooling and coiling processes, and controlling the influence of selective oxidation in the layer cooling and coiling processes: controlling the cooling speed of the laminar cooling to be 70-100 ℃/s in an ultra-fast cooling mode for the laminar cooling; the coiling temperature is controlled to be 550-600 ℃.
Optionally, the multi-stage heating comprises maintaining the temperature at 1200-1220 ℃ for 130-160min.
Optionally, the multi-section heating sequentially includes: the device comprises a preheating section, a first zone heating section, a second zone heating section and a soaking section, wherein the temperature of the preheating section is less than or equal to 800 ℃, the temperature of the first zone heating section is less than or equal to 1150 ℃, the temperature of the second zone heating section is 1200-1220 ℃, and the temperature of the soaking section is 1200-1220 ℃.
Optionally, the preheating section and the one-zone heating section are in oxidizing atmosphere, and the air-fuel ratio of the oxidizing atmosphere is 1.1-1.2; the two-zone heating section and the soaking section adopt reducing atmosphere, and the air-fuel ratio of the reducing atmosphere is 0.9-1.0.
Optionally, a descaling process is used in the rough rolling and the finish rolling.
Compared with the prior art, the technical scheme provided by the embodiment of the application has the following advantages:
the hot-formed steel pickling plate provided by the embodiment of the application is designed by combining chemical components, and the content of C is controlled to be 0.2-0.3%; si element is controlled to be 0.15-0.25%, mn element is controlled to be 1-1.5%, cr element is controlled to be 0.1-0.3%, nb content is properly improved to be 0.02-0.04%, sb element content is added to be 0.03-0.1%, and intergranular oxidation in the steel coiling process is favorably inhibited; because Sb and Nb have lower oxidation potential than iron and are not oxidized, sb and Nb are continuously gathered in a matrix under an iron scale and are enriched to a certain degree, so that the diffusion speed of oxygen to the matrix can be limited, and the effect of inhibiting intergranular oxidation is achieved; while the molten Si-rich sheet iron extends internally along the austenite grain boundaries: the Si element is increased to more than 0.3 percent to form an obvious net-shaped iron sheet shape, the net-shaped Si-rich fayalite diffuses towards the outer iron sheet grain boundary and also spreads towards the inner side of the matrix, so that the surface of the substrate has the defects of cracks, grain boundaries and the like, the Si-rich phase is preferentially oxidized to form an iron sheet anchor embedding shape, and thus the typical shape of intergranular oxidation at a high temperature stage is formed, and the control key points are the control and matching of the Si element in the steel, such as the heating temperature and time; solves the intergranular oxidation of the surface of the hot-formed steel pickled plate and can improve the surface quality and the formability of the pickled plate.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate embodiments consistent with the invention and together with the description, serve to explain the principles of the invention.
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below, and it is obvious for those skilled in the art that other drawings can be obtained according to the drawings without inventive exercise.
FIG. 1 is a schematic flow chart of a method for reducing the intergranular oxidation of the surface of a hot-formed pickled steel plate according to an embodiment of the present disclosure;
FIG. 2 shows the intergranular oxidation morphology of steel at 1200 ℃ for 30min in the examples of the present application;
FIG. 3 shows the intergranular oxidation morphology of steel oxidized at 750 ℃ for 30min in the embodiment of the present application;
FIG. 4 shows the change of the intercrystalline oxidation depth of steel under the condition of air atmosphere oxidation for 30min under different temperature conditions in the embodiment of the application;
FIG. 5 illustrates the inter-rigid oxidation in a comparative example;
FIG. 6 shows the intergranular oxidation after the process of the embodiment of the present application is performed.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present application clearer, the technical solutions in the embodiments of the present application will be clearly and completely described below with reference to the drawings in the embodiments of the present application, and it is obvious that the described embodiments are some embodiments of the present application, but 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 application.
Fig. 1 is a schematic flow chart of an xx method according to an embodiment of the present application.
In one embodiment of the present application, a thermoformed pickled steel sheet has a chemical composition, in mass fractions, comprising: c:0.2-0.3%, si:0.15-0.25%, mn:1-1.5%, cr:0.1-0.3%, nb:0.02 to 0.04%, sb:0.03-0.1%, and the balance of Fe and inevitable impurity elements.
In the embodiment of the present application, according to the characteristics of intergranular oxidation under high temperature conditions, as shown in fig. 2, and the control of the content of the element preferentially oxidized, the temperature and time of the heating furnace are controlled, and the content of the element Si relatively preferentially oxidized is controlled, so as to achieve the purpose of controlling the existence of cracks and grain boundaries on the surface of the substrate.
As an alternative embodiment, the metallographic structure of the hot-formed pickled steel plate comprises, in volume fraction: 10% -20% of ferrite and 80-90% of pearlite.
In the embodiment of the application, in order to ensure the mechanical property of the hot-formed pickled steel plate, the beneficial effect that austenite coarsening in the heat treatment process can be avoided by 10-20% of ferrite and 80-90% of pearlite by volume fraction. In the hot rolling process, the metallographic structure is ferrite or pearlite, and in the heat treatment process, austenite or martensite is formed after austenitizing and water quenching. The metallographic structure in the hot rolling process is normal ferrite and pearlite.
As an alternative embodiment, in the austenite, the austenite element diffusion coefficient at 850 ℃ is: DO- γ =2.47 × 10 -12 ，DSi-γ＝4.06×10 -17 ，DMn-γ＝1.04×10 -17 (ii) a In the ferrite, the diffusion coefficient of ferrite elements at 850 ℃ is as follows: DO-d =2.00 × 10 -11 ；DSi-d＝4.27×10 -15 ；DMn-α＝2.74×10 -15 。
In the embodiment of the present application, a method for reducing the intergranular oxidation of the surface of the hot-formed pickled steel plate is provided, as shown in fig. 1, the method includes the following steps:
s1, obtaining a casting blank containing the chemical components;
s2, measuring and obtaining the nose tip temperature of an intercrystalline oxidation depth curve of the casting blank;
s3, controlling a finish rolling process according to the nose tip temperature;
s4, sequentially carrying out multi-section heating, rough rolling and finish rolling on the casting blank to obtain a rolled casting blank;
s5, calculating and obtaining the austenite element diffusion coefficient and the ferrite element diffusion coefficient of the hot-formed steel pickling plate at a certain temperature;
s6, performing layer cooling and coiling on the rolled casting blank according to the austenite element diffusion coefficient and the ferrite element diffusion coefficient of the hot-formed steel pickling plate to obtain a hot-rolled coil;
and S7, sequentially uncoiling and pickling the hot-rolled coil to obtain the hot-formed steel pickled plate.
In the embodiment of the application, low-temperature intergranular oxidation is formed within the range of 600-800 ℃, as shown in fig. 2, the grain boundary is the weakest place in the metal material, so the oxidation firstly occurs at the grain boundary, after the oxidation of the grain boundary, the oxygen expands to the interior of the grain and oxidizes the whole grain, namely a surface oxidation layer is formed, and the low-temperature intergranular oxidation control lies in the layer cooling and coiling processes.
As an alternative embodiment, the controlling of the finish rolling process according to the nose tip temperature includes:
the nose tip temperature is 750 ℃, the nose tip temperature interval is 700-800 ℃, the nose tip temperature interval is avoided in the finish rolling process, and the influence of low-temperature intergranular oxidation in finish rolling is controlled: the initial rolling temperature of the finish rolling is 1040-1080 ℃, the rolling speed of the finish rolling is controlled to be 8m/s, and the actual final rolling temperature is 880-900 ℃.
In the embodiment of the present application, as shown in fig. 4, the change of the intercrystalline oxidation depth of the steel grade under the condition of air atmosphere oxidation for 30min at different temperatures (600-900 ℃). The nose tip temperature range of the intergranular oxidation depth is about 750 ℃, and is related to the internal and external oxidation competitive relationship of steel grades: if the temperature is higher, the oxygen atom diffusion rate is increased, the external oxidation rate is obviously increased, the inter-crystal oxidation morphology features formed by selective oxidation of alloy elements are replaced by external oxidation burning loss, and the outer-side iron oxide scale is integrally formed, so that the inter-crystal oxidation depth is reduced; if the temperature is lower, the diffusion rate of oxygen in the ferrite body at low temperature is slower, and the effective intergranular oxidation depth can not be formed.
As an optional embodiment, the step of performing layer cooling and coiling on the rolled casting blank according to the austenite element diffusion coefficient and the ferrite element diffusion coefficient of the hot-formed and pickled steel plate comprises:
determining diffusion coefficients of Si, mn and O elements in ferrite and in austenite, determining a ferrite temperature interval and an austenite temperature interval, avoiding the ferrite temperature interval and the austenite temperature interval in the layer cooling and coiling processes, and controlling the influence of selective oxidation in the layer cooling and coiling processes: controlling the cooling speed of the laminar cooling to be 70-100 ℃/s in an ultra-fast cooling mode for the laminar cooling; and controlling the coiling temperature to be 550-600 ℃.
In the embodiment of the application, the intergranular oxidation essentially belongs to the selective internal oxidation category, and the intergranular oxidation elements mainly comprise Si and Mn elements. The diffusion coefficients of O, si and Mn are different between ferrite and austenite, and thus the selective oxidation behavior is different. The diffusion coefficients of Si, mn and O elements in alpha (ferrite) are 1 to 2 orders of magnitude higher than those in gamma (austenite). The final temperature of finish rolling in the hot rolling process is generally set to avoid falling into a two-phase region temperature range, so that the final temperature is higher than the austenitizing temperature, and the influence of selective oxidation of elements in a ferrite body, namely the layer cooling and coiling processes, can be controlled. Because the intergranular oxidation occurs from the grain boundary diffusion of alloy elements and oxygen atoms, the longer-time heat preservation after coiling provides kinetic and thermodynamic conditions for the diffusion, and the intergranular oxidation is inhibited by reducing the coiling temperature and adopting a rapid cooling mode.
As an optional implementation mode, the multi-stage heating comprises heat preservation at 1200-1220 ℃ for 130-160min.
In the embodiment of the application, the steel contains a certain silicon element, the silicon element is easy to form fayalite phase at the interface along with the temperature exceeding 1150 ℃ and is subjected to liquefaction reaction and is diffused into the matrix along the grain boundary, and the diffusion depth of the grain boundary is increased along with the increase of the temperature and the time, so that on the premise of ensuring the thorough burning of the slab, the secondary addition and soaking temperature is controlled, and the total furnace time and the oxygen content in the high-temperature section are controlled.
As an optional embodiment, the multi-stage heating sequentially comprises: the temperature of the preheating section is less than or equal to 800 ℃, the temperature of the first zone heating section is less than or equal to 1150 ℃, the temperature of the second zone heating section is 1200-1220 ℃, and the temperature of the soaking section is 1200-1220 ℃.
In an alternative embodiment, the preheating section and the one-zone heating section are in an oxidizing atmosphere, and the air-fuel ratio of the oxidizing atmosphere is 1.1-1.2; the two-zone heating section and the soaking section adopt reducing atmosphere, and the air-fuel ratio of the reducing atmosphere is 0.9-1.0.
As an alternative embodiment, the rough rolling and the finish rolling use a descaling process.
In the embodiment of the application, the furnace iron sheet is removed by primary descaling after the slab is discharged from the furnace, the rolling process can adopt a 1+5 rolling mode, and a single pass can be adopted: 1. opening coarse descaling for 3 and 5 passes; and starting finish rolling 2, 4 and 6 for double descaling. Through three times of descaling processes, the method is favorable for effectively removing the outside iron scale, on one hand, the method is favorable for improving the surface quality of the hot coil, on the other hand, after the iron scale is removed, the steel plate substrate is more favorable for forming the uniform burning loss of the iron scale in the rolling process, and the fayalite phase distributed along the grain boundary on the surface layer of the plate blank produced in the heating process is removed.
Detailed explanation of the drawings:
the casting blank containing the chemical components of the embodiment of the invention is subjected to a conventional processing technology to obtain the hot-formed pickled steel plate in the prior art, the intergranular oxidation condition of the pickled steel plate is shown in fig. 5, and cracks of surface layer cracking in the stamping process of the pickled steel plate caused by the intergranular oxidation can be observed.
The casting blank containing the chemical components of the embodiment of the invention is processed by the processing technology of the application to obtain the hot-formed pickled steel plate, the condition of the pickled steel plate is as shown in figure 6, no surface layer crack is observed in the stamping process of the pickled steel plate, and the control of the intergranular oxidation phenomenon is proved to be better by the embodiment of the application.
It is noted that, in this document, relational terms such as "first" and "second," and the like, may be used solely to distinguish one entity or action from another entity or action without necessarily requiring or implying any actual such relationship or order between such entities or actions. Also, the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus. Without further limitation, an element defined by the phrases "comprising a," "8230," "8230," or "comprising" does not exclude the presence of additional like elements in a process, method, article, or apparatus that comprises the element.
The foregoing are merely exemplary embodiments of the present invention, which enable those skilled in the art to understand or practice the present invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.
Claims (5)
1. A thermoformed pickled steel sheet having a chemical composition, in mass fractions, comprising: c:0.2-0.3%, si:0.15-0.25%, mn:1-1.5%, cr:0.1-0.3%, nb:
0.02 to 0.04%, sb:0.03-0.1%, the balance being Fe and inevitable impurity elements;
the metallographic structure of the hot-formed pickled steel plate consists of 10-20% of ferrite and 80-90% of pearlite in volume fraction;
among the austenite, the austenite element diffusion coefficient at 850 ℃ is: DO- γ =2.47 × 10 -12 ，DSi-γ＝4.06×10 -17 ，DMn-γ＝1.04×10 -17 (ii) a In ferrite, the diffusion coefficient of ferrite elements at 850 ℃ is: DO- α =2.00 × 10 -11 ；DSi-α＝4.27×10 -15 ：DMn-α＝2.74×10 -15 ；
The method for the intergranular oxidation of the surface of the hot-formed steel pickling plate comprises the following steps:
obtaining a casting blank containing the chemical components;
measuring and obtaining the nose tip temperature of an intercrystalline oxidation depth curve of the casting blank;
controlling a finish rolling process according to the nose tip temperature;
sequentially carrying out multi-section heating, rough rolling and finish rolling on the casting blank to obtain a rolled casting blank;
calculating and obtaining the austenite element diffusion coefficient and the ferrite element diffusion coefficient of the hot-formed acid-pickled steel plate at a certain temperature;
carrying out layer cooling and coiling on the rolled casting blank according to the austenite element diffusion coefficient and the ferrite element diffusion coefficient of the hot-formed steel pickling plate to obtain a hot-rolled coil;
sequentially uncoiling and pickling the hot-rolled coil to obtain a hot-formed steel pickled plate;
and controlling a finish rolling process according to the nose tip temperature, comprising:
the nose tip temperature is 750 ℃, the nose tip temperature interval is 700-800 ℃, the nose tip temperature interval is avoided in the finish rolling process, and the influence of low-temperature intergranular oxidation in finish rolling is controlled: the initial rolling temperature of finish rolling is 1040-1080 ℃, the rolling speed of the finish rolling is controlled to be 8m/s, and the actual finish rolling temperature is 880-900 ℃;
the method is characterized in that the rolled casting blank is subjected to layer cooling and coiling according to the austenite element diffusion coefficient and the ferrite element diffusion coefficient of the hot-formed steel pickling plate, and comprises the following steps: determining diffusion coefficients of Si, mn and O elements in ferrite and in austenite, determining a ferrite temperature interval and an austenite temperature interval, avoiding the ferrite temperature interval and the austenite temperature interval in the layer cooling and coiling processes, and controlling the influence of selective oxidation in the layer cooling and coiling processes: controlling the cooling speed of the laminar cooling to be 70-100 ℃/s in an ultra-fast cooling mode for the laminar cooling; the coiling temperature is controlled to be 550-600 ℃.
2. The hot formed pickled steel sheet of claim 1, wherein the multi-stage heating comprises holding at 1200-1220 ℃ for 130-160min.
3. The hot formed, pickled steel sheet as claimed in claim 1, wherein said multi-stage heating comprises, in sequence: the temperature of the preheating section is less than or equal to 800 ℃, the temperature of the first zone heating section is less than or equal to 1150 ℃, the temperature of the second zone heating section is 1200-1220 ℃, and the temperature of the soaking section is 1200-1220 ℃.
4. The hot formed, pickled steel sheet as claimed in claim 3, wherein said preheating section and said one-zone heating section are in an oxidizing atmosphere, said oxidizing atmosphere having an air-fuel ratio of 1.1 to 1.2; the two-zone heating section and the soaking section adopt reducing atmosphere, and the air-fuel ratio of the reducing atmosphere is 0.9-1.0.
5. The hot formed, pickled steel sheet according to claim 1, wherein said rough and finish rolling are performed by a descaling process.
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| JP5549450B2 (en) * | 2010-07-21 | 2014-07-16 | Ｊｆｅスチール株式会社 | High carbon hot-rolled steel sheet excellent in fine blanking property and manufacturing method thereof |
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