CN115418558B - Method for reducing hot rolling surface warping of acid-resistant steel containing antimony - Google Patents
Method for reducing hot rolling surface warping of acid-resistant steel containing antimony Download PDFInfo
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- CN115418558B CN115418558B CN202210732131.3A CN202210732131A CN115418558B CN 115418558 B CN115418558 B CN 115418558B CN 202210732131 A CN202210732131 A CN 202210732131A CN 115418558 B CN115418558 B CN 115418558B
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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
- 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
- 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
- B22D11/12—Accessories for subsequent treating or working cast stock in situ
- B22D11/122—Accessories for subsequent treating or working cast stock in situ using magnetic fields
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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
- B22D11/16—Controlling or regulating processes or operations
- B22D11/18—Controlling or regulating processes or operations for pouring
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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
- B22D11/16—Controlling or regulating processes or operations
- B22D11/22—Controlling or regulating processes or operations for cooling cast stock or mould
- B22D11/225—Controlling or regulating processes or operations for cooling cast stock or mould for secondary cooling
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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
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
The invention belongs to the technical field of steel rolling, and particularly relates to a method for reducing hot rolled surface skin warping of acid-resistant steel containing antimony. The method comprises the following steps: continuously casting molten steel to obtain a plate blank, wherein the chemical components of the molten steel comprise: calculated by mass fraction, C:0.06-0.08%, mn:1.3% -1.5%, si:0.3% -0.5%, B:0.0005% -0.0010%, sb:0.1% -0.2%, S:0.01-0.02%, ti:0.00005% -0.0001% and the balance of iron and unavoidable impurity elements; and heating, rough rolling, finish rolling and coiling the plate blank to obtain the antimony-containing acid-resistant steel. Through the interaction of the components, the offset polymerization of an Sb interface and the metal state precipitation of b element are reduced, so that the hot-rolled surface skin of the acid-resistant steel containing antimony is reduced.
Description
Technical Field
The invention belongs to the technical field of steel rolling, and particularly relates to a method for reducing hot rolled surface skin warping of acid-resistant steel containing antimony.
Background
Acid-resistant steel has better corrosion resistance in oxidized acid (nitric acid and sulfuric acid), generally stainless steel acid-resistant steel is generally selected, and a large amount of alloy elements are added to have the effect of corrosion resistance. In a dry-wet alternating environment, such as an atmospheric corrosion environment, after a certain amount of Cr, ni, cu and P elements are added, the corrosion resistance of steel in ocean or industrial atmosphere is obviously improved, and the main way of improving the corrosion resistance is to enrich the added elements in an inner rust layer and promote the generation of alpha-FeOOH with better protectiveness, so that the invasion of corrosive media is inhibited. The Sb element can improve the corrosion resistance of the steel, for example, after a trace amount of Sb element is added into the steel in a strong acid environment, a compact protective film can be formed on the surface of the steel, and the passivation of the anode is promoted, so that the dissolution of the anode is inhibited. The addition of the Sb element promotes the generation of alpha-FeOOH, and meanwhile, the Sb element forms Sb in an acidic environment 2 O 5 The product is compact, and can promote passivation of the surface of the steel plate and inhibit anodic dissolution. However, after certain Sb element is added into the steel grade, the surface skin warping condition in the hot rolling process is more easy to occur.
Disclosure of Invention
The application provides a method for reducing the hot-rolled surface skin of acid-resistant steel containing antimony, which aims to solve the technical problem of reducing the hot-rolled surface skin of acid-resistant steel containing antimony.
In a first aspect, the present application provides a method for reducing hot rolled surface skin of acid resistant steel containing antimony, the method comprising the steps of:
continuously casting molten steel to obtain a plate blank, wherein the chemical components of the molten steel comprise: calculated by mass fraction, C:0.06-0.08%, mn:1.3% -1.5%, si:0.3% -0.5%, B:0.0005% -0.0010%, sb:0.1% -0.2%, S0.01-0.02%, ti:0.00005% -0.0001% and the balance of iron and unavoidable impurity elements;
and heating, rough rolling, finish rolling and coiling the plate blank to obtain the antimony-containing acid-resistant steel.
Optionally, the continuous casting adopts a weak cooling process, wherein in the continuous casting, the pulling speed is 1.0-2.5 m/min, and the cold water strength is 0.5-2.0L/kg.
Optionally, the stirring current intensity of the continuous casting is 200-800A, and the frequency is 2-6 Hz.
Optionally, the heating includes a first heating section, a second heating section and a soaking section, and the total heating time is 140-160min.
Optionally, the time of the first heating section is less than 50min, and the outlet temperature of the first heating section is 800-900 ℃.
Optionally, the target temperature of the second heating section is 1100-1200 ℃.
Optionally, the temperature of the soaking section is 1200-1220 ℃, and the soaking section adopts weak reducing atmosphere, wherein the lambda value is 0.8-1.0.
Optionally, in the rough rolling, a descaling process is adopted, the times of the dephosphorization process are more than or equal to 4, and the pressure of the dephosphorization process is more than 20MPa.
Optionally, the inlet temperature of the finish rolling is 1050-1070 ℃, and the finish rolling temperature of the finish rolling is 900-920 ℃.
Optionally, the coiling adopts a front-stage cooling mode, and the temperature of the coiling is 620-660 ℃.
Compared with the prior art, the technical scheme provided by the embodiment of the application has the following advantages:
according to the method provided by the embodiment of the application, molten steel is continuously cast to obtain a plate blank, and the chemical components of the molten steel comprise: calculated by mass fraction, C:0.06-0.08%, mn:1.3% -1.5%, si:0.3% -0.5%, B:0.0005% -0.0010%, sb:0.1% -0.2%, S0.01-0.02%, ti:0.00005% -0.0001% and the balance of iron and unavoidable impurity elements; and heating, rough rolling, finish rolling and coiling the plate blank to obtain the antimony-containing acid-resistant steel. The content of each component is controlled to act on the Sb interface segregation to control the metal state precipitation condition of the Sb element, and meanwhile, the preparation process is matched to reduce the Sb interface segregation and the metal state precipitation of the b element, so that the hot-rolled surface skin of the acid-resistant steel containing antimony is reduced.
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 invention or the technical solutions in the prior art, the following description will briefly explain the drawings used in the embodiments or the description of the prior art, and it will be obvious to those skilled in the art that other drawings can be obtained from these drawings without inventive effort.
FIG. 1 is a schematic flow chart of a method for reducing hot rolled surface skin of acid resistant steel containing antimony according to an embodiment of the present application;
FIG. 2 is a macro-topography of a comparative surface skin-lifting;
FIG. 3 is a surface microfeature of a comparative surface skin;
FIG. 4 is a cross-sectional spectroscopy analysis of a comparative example;
fig. 5 is an example surface microfeature.
Detailed Description
For the purposes of making the objects, technical solutions and advantages of the embodiments of the present application more clear, the technical solutions of 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 apparent that the described embodiments are some embodiments of the present application, but not all embodiments. All other embodiments, which can be made by one of ordinary skill in the art without undue burden from the present disclosure, are within the scope of the present application based on the embodiments herein.
In a first aspect, the present application provides a method for reducing hot rolled surface skin of acid resistant steel containing antimony, as shown in fig. 1, the method comprising the steps of:
s1, continuously casting molten steel to obtain a plate blank, wherein the chemical components of the molten steel comprise: calculated by mass fraction, C:0.06-0.08%, mn:1.3% -1.5%, si:0.3% -0.5%, B:0.0005% -0.0010%, sb:0.1% -0.2%, S0.01-0.02%, ti:0.00005% -0.0001% and the balance of iron and unavoidable impurity elements;
the principle of adding trace Ti is as follows: the Sb element is biased to the gamma grain boundary in the continuous casting cooling process, when the concentration of the Sb element exceeds the upper limit of solubility in iron, the Sb element is concentrated in the grain boundary in the form of simple substances or compounds formed among the Sb element and the compound, and trace Ti is added to perform precipitation strengthening, so that the Sb element is reduced to the gamma grain boundary in the continuous casting cooling process, and the surface warping is effectively reduced.
S2, heating, rough rolling, finish rolling and coiling the plate blank to obtain the acid-resistant steel containing antimony.
In this embodiment, the effect of each element on Sb interface segregation:
element Sb: in the heating process of the steel plate, a large amount of iron scales are formed on the surface, the steel seeds Sb are not easy to oxidize, and the surface layer enrichment morphology characteristic is easy to form. And if the metal content exceeds the solubility in iron, a liquefied phase is formed between the scale and the matrix. The defect positions are all related to a large amount of Sb element residues and liquefaction, and the problem of cracking in the rolling process caused by embrittlement of austenite grain boundaries is solved, so that the content of the Sb element is 0.1-0.2%.
Si element: the addition of Si reduces the amount of Sb-rich phase at the steel/iron interface, which helps to reduce the surface hot embrittlement sensitivity. Internal oxidation of Si is believed to be the primary cause of reducing the number of Sb-rich phases. At a temperature of 1177 ℃ or higher (FeO-2 FeO.SiO) 2 Eutectic temperature), fe 2 SiO 4 The liquid phase is formed, the liquid phase layer seals the steel/iron sheet interface, and the oxidation rate at 1200 ℃ is increased, and meanwhile, the occlusion of Sb in the iron sheet is increased, so that the amount of the Sb-rich liquid phase is reduced, and the content of Si element is 0.3% -0.5%.
B element: due to the addition of B, wettability of Sb liquid phase with γ grain boundary is reduced. Therefore, the brittleness-inhibiting effect of the B addition is considered to be due to the reduced grain boundary wettability and the reduced amount of Sb concentrated phase, and thus the content of B element is 0.0005% to 0.0010%.
Mn/S element: the MnS can become heterogeneous nuclei of Sb, and the Sb is precipitated on the MnS, so that the S content is properly increased, and the quantity of the sulfide fierce inclusions can be increased, thereby effectively reducing the enrichment segregation of the Sb in an oxide layer and improving the plasticity of the steel, and the content of Mn element is 1.3-1.5%, and the content of B element is 0.0005-0.0010%.
In some embodiments, the continuous casting adopts a weak cooling process, wherein the drawing speed in the continuous casting is 1.0-2.5 m/min, and the cold water strength is 0.5-2.0L/kg.
In order to avoid thermal embrittlement caused by massive precipitation and invasion of metal Sb into grain boundaries, the continuous casting adopts a weak cooling process, for example, the drawing speed in the continuous casting is not in the range, and the method has the adverse effect of inducing edge cracking in the continuous casting process, for example, the cold water strength is not in the range, and the adverse effect of falling the edge temperature into a steel grade brittleness interval.
The principle of adopting the weak cooling process for continuous casting is as follows: the corner regions at both sides of the cold section continuous casting blank are in a strong oxidizing atmosphere environment, the corners are oxidized more seriously, liquid Sb enrichment is easier to form and permeate towards gamma grain boundaries, the grain boundary binding force is reduced sharply, meanwhile, the transformation temperature of gamma to alpha is delayed, the gamma grain boundaries are in a film alpha in a very wide temperature range, the ferrite phase strength is only 1/4 of the austenite phase, and the strain rate is 10 -4 ～10 -2 When the stress exceeds the strength which can be borne by the ferrite phase of the grain boundary, a cavity is generated in the ferrite to form a corner crack in the continuous casting process, so that the pulling speed is controlled to be 1.0-2.5 m/min and the cold water strength is controlled to be 0.5-2.0L/kg in the continuous casting.
In some embodiments, the stirring current intensity of the continuous casting is 200-800A, and the frequency is 2-6 Hz.
In order to improve initial solidification uniformity, an electromagnetic stirring technology of a slab crystallizer is applied, the stirring current intensity is controlled to be 200-800A, and the frequency is controlled to be 2-6 Hz, so that a strong magnetic field is generated in molten steel to be cooled and solidified, and a liquid direction part can move directionally and rotate through interaction of induced currents flowing in the molten steel, so that the liquid-phase molten steel in a casting blank is stirred, the effects of element homogenization and fine solidification structure are achieved, fluctuation of the liquid surface of the crystallizer caused by overlarge electromagnetic stirring force is avoided, and the positive effects of element homogenization and grain boundary precipitation embrittlement grain boundary are achieved.
In some embodiments, the heating comprises a first heating section, a second heating section, and a soaking section, and the total time of heating is 140-160min.
In some embodiments, the first heating stage has a time of < 50 minutes and an outlet temperature of the first heating stage is 800-900 ℃.
In some embodiments, the target temperature of the second heating section is 1100-1200 ℃.
In some embodiments, the soaking stage has a temperature of 1200-1220 ℃, and the soaking stage adopts a weak reducing atmosphere, wherein lambda value is 0.8-1.0.
Specifically, under the condition of reducing atmosphere, the lambda value is controlled to be 0.8-1.0, so that oxidation burning loss and interfacial enrichment precipitation of Sb element can be reduced, and the influence of surface warping is effectively avoided.
In order to avoid the increase of the enrichment amount of grain boundaries and surface layers in the Sb element heating process, the time and the temperature of the first heating section, the second heating section and the soaking section are controlled, so that the surface warping is further avoided.
The principle of controlling time is described by combining the characteristic of unbalanced segregation of Sb element: explained by using a vacancy-atomic model, as isothermal time is prolonged, solute Sb processes predominate, vacancies disappear at grain boundaries due to disintegration of the complex at the grain boundaries, excess solute atoms remain at the crystal-vacancy complex carrying solute atoms to the grain boundaries, and thus the amount of segregation of elements increases rapidly, and when critical time is reached, the amount of segregation reaches a maximum: when the isothermal time is further prolonged, single Sb atoms move from grain boundaries to deagglomeration boundaries within the crystal and regions near the grain boundaries, thereby forming unbalanced segregation.
The principle of temperature control is described by using a high temperature thermoplastic experiment: the plastic change of the steel grade is analyzed, and the plastic is obviously reduced to below 40% in the range of 900-1000 ℃, and the straightening section and the hot rolling rough rolling fixed width and the finish rolling large reduction pass in the continuous casting process are prevented from falling into the temperature range.
In the whole, the plastic change of the steel grade is analyzed by utilizing a high-temperature thermoplastic experiment, and the plastic change is obviously reduced in the range of 900-1000 ℃, so that the high Wen Duanmian shrinkage of the steel grade is reduced to below 40%, and the straightening section, the hot-rolling rough rolling width setting and the finish rolling large reduction pass in the continuous casting process are prevented from falling into the temperature range.
In some embodiments, in the rough rolling, a descaling process is adopted, the number of times of the dephosphorization process is more than or equal to 4, and the pressure of the dephosphorization process is more than 20MPa.
It should be noted that: 4 or more passes of descaling can be adopted, and especially the odd-even pass is matched with the descaling, so that 3 passes are ensured by a thin specification.
The method also comprises the following steps: the thickness of the intermediate billet in the rolling process is controlled to be 34-38mm, so that the total compression in the finish rolling process is reduced, and cracking is avoided.
In some embodiments, the finish rolling has an inlet temperature of 1050-1070 ℃ and a finish rolling temperature of 900-920 ℃.
The finish rolling inlet temperature is further increased, the plasticity of the steel grade can be ensured, and meanwhile, the surface cracking caused by the larger rolling load in the finish rolling process is avoided; the rolling load of the finish rolling process F2 and F3 can be reduced, and the rolling reduction is controlled to be 40-45% and 30-35% respectively.
In some embodiments, the coiling employs a front stage cooling mode, the temperature of the coiling being 620-660 ℃.
The adoption of the front section cooling mode has the beneficial effect of avoiding the segregation of the Sb element grain boundary; the coiling temperature is 620-660 ℃, the range of 900-1000 ℃ can be avoided, and the situation that the plasticity is obviously reduced is avoided.
The method of the present invention will be described in detail with reference to examples, comparative examples and experimental data.
The surface skin-warping characteristics of the antimony-containing acid-resistant steel are shown in table 1, and the content of each element in mass fraction is shown in table 2. The depth of the Sb element is measured by adopting a glow discharge spectrum method, and the position of the glow spectrum, in which the content of the Sb element is reduced to 30% of the maximum value, is taken as the position of the distribution of the Sb element. The pictures are obtained by observing and measuring with a scanning electron microscope.
Table 1 the component content and the surface Sb precipitation content of the example group and the comparative example group.
Table 2 the process for preparing the steel sheets of the example group and the comparative example group.
The surface skin appearance and quality of the antimony-containing acid-resistant steel prepared according to the process parameters in the above examples and comparative examples were evaluated. The crack length of the surface of the bent outer edge was observed by a scanning electron microscope, the maximum value of the crack length was measured in 5 fields of view, and then the average value of the maximum values was taken as the surface crack length, and the experimental results are shown in table 3.
Table 3 experimental results of the steel plates of the example group and the comparative example group.
As is clear from Table 3, the crack length of the steel sheet is 0 to 5 μmBetween, average every 5mm 2 The number of surface cracks in the steel sheet was 0-1.7, while the crack length of the comparative example group was 20-60 μm, on average every 5mm 2 The number of surface cracks appearing in the steel plate is 4-8, which indicates that the steel plate of the example group is not easy to appear surface cracks, and the steel plate has good surface quality after forming, and the bending angle after cold-finishing experiment is 180.
Detailed description of the drawings 2-5:
as shown in fig. 2 and 3, the macro-topography of the skin-lifting surface of the comparative example is shown, wherein fine lines and small skin-lifting defects are formed on the surface of the hot rolled plate along the rolling direction. Crack surrounding oxide particle information: the periphery of the crack has no obvious oxidation dot morphology features with large size and certain thickness; the local position of the interface between the side position matrix and the oxide scale has obvious metal element enrichment morphology features (white and bright positions).
As shown in fig. 4, which is a microscopic feature of the surface of the skin of the comparative example, a bright white metal luster is provided around the cracks in the figure as an Sb element enrichment region, which illustrates that Sb is seriously enriched in the surface layer to embrittle the surface layer grains during the rolling process, so as to cause cracking during the rolling process.
As shown in fig. 5, the energy spectrum analysis of the section of the skin of the comparative example shows that the metal state precipitation condition of the Sb element exists at the white and bright positions. The source of the surface seesaw is from the metallic precipitation of the surface Sb element. The elemental content of each point in the graph is shown in table 4.
Table 4 shows the analysis results of the section energy spectrum of the skin of the comparative example.
As can be seen from Table 4, sb is distributed in all of the spectrogram 1, the spectrogram 2 and the spectrogram 6, and the distribution amount is higher in the spectrogram 3, which shows that the origin of the surface skin warpage is from the metal state precipitation of the Sb element on the surface. Wherein, the Fe element is reduced to about 60 percent, which indicates that the Fe-Sb composite phase is precipitated. Fig. 5 is a microscopic view of the surface of the example, showing good microscopic effects.
It should be noted that in this document, relational terms such as "first" and "second" and the like are 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. Moreover, 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 phrase "comprising one … …" does not exclude the presence of other like elements in a process, method, article, or apparatus that comprises the element.
The foregoing is only a specific embodiment of the invention to enable those skilled in the art to understand or practice the 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 (1)
1. A method for reducing hot rolled surface skin of acid resistant steel containing antimony, the method comprising the steps of:
continuously casting molten steel to obtain a plate blank, wherein the chemical components of the molten steel comprise: calculated by mass fraction, C:
0.06-0.08%, mn:1.3% -1.5%, si:0.3% -0.5%, B:0.0005% -0.0010%, sb:0.1% -0.2%, S:0.01-0.02%, ti:0.00005% -0.0001% and the balance of iron and unavoidable impurity elements;
heating, rough rolling, finish rolling and coiling the slab to obtain the acid-resistant steel containing antimony;
the heating comprises a first heating section, a second heating section and a soaking section, and the total heating time is 140-160min; the time of the first heating section is less than 50min, and the outlet temperature of the first heating section is 800-900 ℃;
the target temperature of the second heating section is 1100-1200 ℃;
the temperature of the soaking section is 1200-1220 ℃, and the soaking section adopts weak reducing atmosphere, wherein the lambda value is 0.8-1.0;
the continuous casting adopts a weak cooling process, wherein in the continuous casting, the pulling speed is 1.0-2.5 m/min, and the cold water strength is 0.5-2.0L/kg; the stirring current intensity of the continuous casting is 200-800A, and the frequency is 2-6 Hz; in the rough rolling, a descaling process is adopted, the times of the dephosphorization process are more than or equal to 4, and the pressure of the dephosphorization process is more than 20MPa;
the inlet temperature of the finish rolling is 1050-1070 ℃, and the finish rolling temperature of the finish rolling is 900-920 ℃;
the coiling adopts a front-stage cooling mode, and the temperature of the coiling is 620-660 ℃.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210732131.3A CN115418558B (en) | 2022-06-21 | 2022-06-21 | Method for reducing hot rolling surface warping of acid-resistant steel containing antimony |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210732131.3A CN115418558B (en) | 2022-06-21 | 2022-06-21 | Method for reducing hot rolling surface warping of acid-resistant steel containing antimony |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN115418558A CN115418558A (en) | 2022-12-02 |
| CN115418558B true CN115418558B (en) | 2023-07-11 |
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| CN202210732131.3A Active CN115418558B (en) | 2022-06-21 | 2022-06-21 | Method for reducing hot rolling surface warping of acid-resistant steel containing antimony |
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| KR100711358B1 (en) * | 2005-12-09 | 2007-04-27 | 주식회사 포스코 | High strength cold rolled steel sheet and hot dip galvanized steel sheet having excellent formability, bake hardenability and plating property, and the method for manufacturing thereof |
| JP4811528B2 (en) * | 2009-07-28 | 2011-11-09 | Ｊｆｅスチール株式会社 | High-strength cold-rolled steel sheet and manufacturing method thereof |
| KR102165051B1 (en) * | 2016-03-31 | 2020-10-13 | 제이에프이 스틸 가부시키가이샤 | Thin steel sheet and plated steel sheet, and manufacturing method of thin steel sheet and plating steel sheet |
| JP6589903B2 (en) * | 2017-02-06 | 2019-10-16 | Ｊｆｅスチール株式会社 | Hot-dip galvanized steel sheet and manufacturing method thereof |
| CN109112433B (en) * | 2017-06-26 | 2019-09-20 | 鞍钢股份有限公司 | Without 590MPa grades of cold-rolled biphase steels of striated surface defect and production method |
| CN108251764A (en) * | 2018-03-15 | 2018-07-06 | 马钢(集团)控股有限公司 | One kind is containing the strong 350MPa grades high anti-corrosion hot rolled H-shaped and its production method of antimony surrender |
| WO2020250735A1 (en) * | 2019-06-14 | 2020-12-17 | Ｊｆｅスチール株式会社 | High-strength hot-rolled steel sheet and method for manufacturing same |
| CN113020257B (en) * | 2019-12-09 | 2022-08-12 | 上海梅山钢铁股份有限公司 | Method for eliminating surface warping defect of weather-resistant steel plate blank in hot rolling process |
| WO2022014131A1 (en) * | 2020-07-14 | 2022-01-20 | Ｊｆｅスチール株式会社 | Continuous annealing apparatus, continuous hot-dip galvanizing apparatus, and method for manufacturing steel sheet |
| CN114058949B (en) * | 2021-10-18 | 2022-10-21 | 首钢集团有限公司 | Hot-forming steel pickling plate and method for reducing intercrystalline oxidation of surface of steel pickling plate |
| CN114058951B (en) * | 2021-10-19 | 2023-04-07 | 首钢集团有限公司 | 65Mn saw blade steel and preparation method thereof |
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