CN115584438A - Ultrahigh carbon steel plate and manufacturing method thereof - Google Patents
Ultrahigh carbon steel plate and manufacturing method thereof Download PDFInfo
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Images
Classifications
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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
-
- 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
- B22D11/10—Supplying or treating molten metal
- B22D11/11—Treating the molten metal
- B22D11/111—Treating the molten metal by using protecting powders
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/0006—Adding metallic additives
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/0025—Adding carbon material
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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 application provides an ultra-high carbon steel plate and a manufacturing method thereof, wherein the ultra-high carbon steel plate comprises the following chemical elements in percentage by mass: c:1.15% -1.5%, preferably 1.15% -1.25%; si:0.1 to 0.35 percent, preferably 0.1 to 0.25 percent; mn:0.1% -0.4%, preferably 0.3% -0.4%; and Als:0.02 to 0.05%, preferably 0.02 to 0.03%; p:0 to 0.03%, preferably 0 to 0.015%; s:0 to 0.03%, preferably 0 to 0.004%; the balance being Fe and unavoidable impurity elements. According to the method for manufacturing the ultra-high carbon steel plate based on the thin slab continuous casting and rolling process, the chemical element composition of the ultra-high carbon steel plate is optimized, the production process is optimized, the number of inclusions and element segregation are reduced, and the ultra-high carbon steel plate with a small decarburized layer depth and high strength is obtained.
Description
Technical Field
The application relates to the technical field of high-carbon tool steel production, in particular to an ultrahigh-carbon steel plate and a manufacturing method thereof.
Background
The ultra-high carbon steel refers to plain carbon steel with the carbon content of 1.0-2.1% and the cementite volume percentage of 15-32%. The ultrahigh carbon steel plate has excellent technological properties and room temperature mechanical properties. The ultra-high carbon steel plate with good comprehensive performance has great development space and application prospect in the aspects of being used as wear-resistant materials, tools and dies and structural materials.
At present, the production technology of ultrahigh carbon steel at home and abroad mainly adopts the traditional thick slab hot continuous rolling production technology, and the problems of poor stability of molten steel chemical components, serious casting blank element segregation, deep decarburization layer on the surface of a steel plate, poor performance stability and large difficulty of rolling thin specifications exist in the production process, so that the problems of incomplete annealing and spheroidizing or uneven quenching hardness of the steel plate after annealing or tempering treatment of the steel plate are caused. The application provides an ultra-high carbon steel plate and a method for manufacturing the ultra-high carbon steel plate based on a thin slab continuous casting and rolling (CSP) process.
Disclosure of Invention
The application provides an ultra-high carbon steel plate and a method for manufacturing the same based on a thin slab continuous casting and rolling process, wherein the ultra-high carbon steel plate can reduce the number and segregation of inclusions and has high strength.
In a first aspect, the present application provides an ultra-high carbon steel sheet, which comprises the following chemical elements in percentage by mass:
c:1.15% -1.5%, preferably 1.15% -1.25%;
si:0.1 to 0.35 percent, preferably 0.1 to 0.25 percent;
mn:0.1 to 0.4 percent, preferably 0.3 to 0.4 percent;
and (3) Als:0.02 to 0.05%, preferably 0.02 to 0.03%;
p:0 to 0.03%, preferably 0 to 0.015%;
s:0 to 0.03%, preferably 0 to 0.004%;
the balance being Fe and unavoidable impurity elements.
Among the technical scheme of this application, chemical element composition through to super high carbon steel sheet material optimizes, reduces inclusion quantity and elemental segregation, especially through optimizing the mass ratio of C, si, als, when the addition of suitable Si, als restraines netted carbide and separates out, need not additionally to add carbide stabilization element and just can avoid the emergence of graphitization, and suitable C content can guarantee to obtain the super high carbon steel sheet material that has higher strength.
In some embodiments of the present application, a ratio of a depth of the decarburized layer of the ultra-high carbon steel sheet to a thickness of the ultra-high carbon steel sheet is 0.15% or less.
In some embodiments of the present application, the grade of the type B inclusions in the ultra-high carbon steel sheet is less than or equal to 0.5; the grade of the D-type inclusion is less than or equal to 1.
In some embodiments of the present application, the Rockwell hardness difference of the ultra-high carbon steel plate after quenching is less than or equal to 2.2.
In some embodiments of the present application, the yield strength R of the ultra high carbon steel sheet el ≥850MPa；
Optionally, the tensile strength R of the ultrahigh carbon steel plate m ≥1250MPa；
Optionally, the elongation after fracture of the ultrahigh carbon steel plate is more than or equal to 8%.
In a second aspect, the present application provides a method for manufacturing an ultra-high carbon steel plate based on a thin slab continuous casting and rolling process, comprising the following steps:
s10: performing converter smelting on the raw materials by using a slag-remaining double-slag method to obtain molten steel, wherein the content of C in the molten steel is more than 0.3 percent and the content of P in the molten steel is less than 0.01 percent in terms of mass fraction;
s20: adding a carburant and an alloy material into the molten steel, and refining to obtain alloyed molten steel with the chemical element composition according to any one of the embodiments of the first aspect;
s30: and carrying out continuous casting treatment on the alloyed molten steel to obtain a casting blank.
According to the technical scheme, the ultrahigh-carbon steel plate is manufactured based on a thin slab continuous casting and rolling process, the C content in molten steel obtained by smelting in a converter is controlled to be more than 0.3%, the P element is controlled to be less than 0.01%, the oxidability of the molten steel is controlled, deoxidation products are reduced, the cleanliness of the molten steel is improved, the addition amount of a carburant can be reduced, and alloyed molten steel with chemical element composition in the first aspect embodiment is obtained through refining treatment, so that the number of inclusions in the ultrahigh-carbon steel plate is remarkably reduced, and the thin ultrahigh-carbon steel plate with high strength is obtained.
In some embodiments of the present application, in the step S30, the viscosity of the continuous casting mold flux is 0.012 to 0.13Pa · S, the melting temperature is 710 to 850 ℃, and the basicity is 0.8 to 1 in the continuous casting process.
In some embodiments of the present application, the continuous casting mold flux specifically includes: 12.5-16.5% by mass of Na 2 O，2％～4％Li 2 O，8.5％～15.5％F - ；
Preferably, the continuous casting mold flux specifically includes: 14.5 to 16% by mass of Na 2 O，2％～3.5％Li 2 O，12％～14％F - 。
In some embodiments of the present application, in the step S30, the specific water amount in the continuous casting secondary cooling zone in the continuous casting process is 1.6 to 1.7L/(kg · min).
In some embodiments of the present application, the method of manufacturing further comprises the steps of:
s40: and heating, dephosphorizing, rolling, cooling and coiling the casting blank to obtain the ultrahigh carbon steel plate.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate embodiments consistent with the present application and together with the description, serve to explain the principles of the application.
Fig. 1 is a metallographic structure diagram of an ultra-high carbon steel plate in example 1.
Fig. 2 is a metallographic structure diagram of the ultra-high carbon steel sheet in example 2.
Fig. 3 is a metallographic structure diagram of the ultra-high carbon steel sheet in example 3.
Fig. 4 is a metallographic structure diagram of the ultra-high carbon steel sheet in comparative example 1.
With the above figures, there are shown specific embodiments of the present application, which will be described in more detail below. The drawings and written description are not intended to limit the scope of the inventive concepts in any manner, but rather to illustrate the concepts of the application by those skilled in the art with reference to specific embodiments.
Detailed Description
The examples or embodiments are described in a progressive arrangement throughout this specification, each with emphasis on illustrating differences from the other examples.
In the description herein, references to the description of the terms "one embodiment," "some embodiments," "an illustrative embodiment," "an example," "a specific example," or "some examples" or the like mean that a particular feature, structure, material, or characteristic described in connection with the embodiment or example is included in at least one embodiment or example of the present application. In this specification, schematic representations of the above terms do not necessarily refer to the same embodiment or example. Furthermore, the particular features, structures, materials, or characteristics described may be combined in any suitable manner in any one or more embodiments or examples.
Furthermore, the terms "first", "second" and "first" are used for descriptive purposes only and are not to be construed as indicating or implying relative importance or implicitly indicating the number of technical features indicated. Thus, a feature defined as "first" or "second" may explicitly or implicitly include at least one of the feature. In the description of the present application, "plurality" means at least two, e.g., two, three, etc., unless specifically limited otherwise.
The applicant finds that the existing domestic and overseas ultrahigh carbon steel production technology mainly adopts the traditional thick slab hot continuous rolling production technology, and the problems of poor molten steel chemical composition stability, serious casting blank element segregation, deep steel plate surface decarburization layer, poor performance stability and large rolling thin specification difficulty exist in the production process, so that the problems of incomplete steel plate annealing spheroidization or uneven quenching hardness after steel plate annealing or quenching and tempering are caused.
Therefore, the applicant firstly uses the thin slab continuous casting and rolling process to manufacture the ultrahigh carbon steel plate, optimizes the chemical composition of the ultrahigh carbon steel plate, and optimizes the process parameters of the manufacturing method at the same time, thereby obtaining the thin ultrahigh carbon steel plate with good performance.
In a first aspect, the present application provides an ultra-high carbon steel sheet, which comprises the following chemical elements in percentage by mass:
c:1.15% -1.5%, preferably 1.15% -1.25%;
si:0.1 to 0.35 percent, preferably 0.1 to 0.25 percent;
mn:0.1% -0.4%, preferably 0.3% -0.4%;
and Als:0.02 to 0.05%, preferably 0.02 to 0.03%;
p:0 to 0.03%, preferably 0 to 0.015%;
s:0 to 0.03%, preferably 0 to 0.004%;
the balance being Fe and unavoidable impurity elements.
In the technical scheme of this application, chemical element through to the ultra high carbon steel sheet material constitutes and optimizes, reduces inclusion quantity and element segregation, especially through optimizing the mass ratio of C, si, als, when the addition amount of suitable Si, als suppresses the net carbide and separates out, does not need additionally to add carbide stabilizing element and just can avoid the emergence of graphitization, and suitable C content can guarantee to obtain the ultra high carbon steel sheet material that has higher strength.
The chemical composition and content in the technical scheme of the application are explained in detail below.
The content of C is set in the range of 1.15% -1.5%:
carbon (C) plays a role in solid solution strengthening in steel, the content is increased, the strength, the hardness and the wear resistance are improved, however, too high content easily generates network carbide, so that the ductility and toughness are low, the brittleness is high, the carbon content of the ultra-high carbon steel plate is 1% -2.1%, in the technical scheme of the application, in order to reduce the problems of inclusions and chemical components in the ultra-high carbon steel plate, the strength and the wear resistance of the steel are considered, the C content is controlled within the range of 1.15% -1.5%, too low content can cause that the strength cannot meet the requirement, and too high content can cause that the ductility and toughness are poor and the processing is difficult.
In some embodiments of the present application, the C content may also be set within a range of 1.15% to 1.25%.
The Si content is set in the range of 0.1-0.35%:
silicon (Si) can obviously improve A in the ultra-high carbon steel plate 1 Temperature, inhibiting cementite coarsening, expanding the temperature range of superplastic forming, effectively inhibiting the precipitation of pre-eutectoid net-shaped carbide, but easily causing graphitization when the adding amount is too high, and easily generating cracks during processingThe Si content is controlled to be 0.1-0.35%, and in addition, the precipitation of reticular carbides is reduced by reducing the C content and adding Als, so that the plasticity of the ultrahigh carbon steel plate is ensured.
In some embodiments of the present application, the Si content may also be set within a range of 0.1% to 0.25%.
The Mn content is set within the range of 0.1% -0.4%:
manganese (Mn) is mainly used in the ultra-high carbon steel sheet to improve hardenability and effectively suppress the influence of trace harmful elements such as S, but when the amount is too high, the structure of the steel is coarse, and thus the Mn content is controlled to 0.1% to 0.4%.
In some embodiments of the present application, the Mn content may also be set within a range of 0.3% to 0.4%.
The Als content is set in the range of 0.02-0.05%:
acid-soluble aluminum (Als) as ferrite-forming element can significantly increase A 1 The superplastic application temperature range of the ultrahigh carbon steel plate is expanded, the addition of Als can obviously refine the interlayer spacing of pearlite plates, inhibit the precipitation of reticular carbides and refine carbide particles, and has a promoting effect on carbide spheroidization; in addition, although the ultra-high carbon steel sheet has a deoxidation effect during the manufacturing process, thereby inhibiting oxygen from forming various inclusions in the steel and improving the purity of molten steel, the content of Als is controlled within a range of 0.02 to 0.05% by promoting the formation of graphite.
In some embodiments of the present application, the content of Als may also be set in the range of 0.02 to 0.03%.
The content of P and S is controlled to be below 0.03 percent:
phosphorus (P) and sulfur (S) are two harmful elements in high-strength steel, and P can cause cold brittleness of the steel, reduce the toughness and plasticity of the steel and obviously reduce the low-temperature impact property of the steel; s forms MnS inclusions with manganese in steel, the cold processing capability of the steel is obviously reduced, and S also consumes Ti elements in the steel and reduces the effective Ti content in the steel; reducing the P and S content increases the metallurgical cost, so the content of both alloying elements is generally controlled to a certain extent. Therefore, in the technical scheme of the application, the content of P and S is controlled to be less than 0.03 percent, so that the influence of P and S on the performance of the high-strength steel is reduced to the lowest possible level.
In some embodiments of the present application, the P content may also be controlled below 0.015% and the S content below 0.004%.
In some embodiments of the present application, the ratio of the depth of the decarburized layer of the ultra-high carbon steel sheet to the thickness of the ultra-high carbon steel sheet is 0.15% or less.
In some embodiments, the ratio of the depth of the decarburized layer of the ultra-high carbon steel plate to the thickness of the ultra-high carbon steel plate is less than or equal to 0.15%, the depth of the decarburized layer can reduce the quenching hardness and the wear resistance of the ultra-high carbon steel plate, and can reduce the fatigue strength of steel.
In some embodiments of the present application, the grade of the type B inclusion in the ultra-high carbon steel sheet is less than or equal to 0.5; the grade of the D-type inclusion is less than or equal to 1.
In some of the above embodiments, the type B inclusions are alumina inclusions, the type D inclusions are spherical oxide inclusions, the higher the grade of the type B inclusions is, the larger the number of the inclusions is, or the size of the spherical oxide inclusions is, and the inclusions have adverse effects on the strength, the plasticity and the toughness of the ultra-high carbon steel plate, the type B inclusion grade in the ultra-high carbon steel plate provided by the present application is less than or equal to 0.5, the type D inclusion grade in the ultra-high carbon steel plate is less than or equal to 1, the low number of the inclusions and the small size of the inclusions are indicated, and therefore the influence on the performance of the steel is small.
In some embodiments of the present application, the Rockwell hardness difference of the ultra-high carbon steel sheet after quenching is less than or equal to 2.2.
In some embodiments, the rockwell hardness difference of the quenched ultra-high carbon steel plate is less than or equal to 2.2, which indicates that the structure performance of the ultra-high carbon steel plate is uniform, wherein chemical elements are not obviously segregated, so that the ultra-high carbon steel plate provided by the application has stable performance and uniform structure performance.
As shown in fig. 1 to 3, which are metallographic structure diagrams of the ultra-high carbon steel plate prepared in the examples of the present application, it can be seen that the ultra-high carbon steel plate prepared in each example has uniform structure properties and few inclusions, and thus it can be seen that the ultra-high carbon steel plate provided by the present application has a low inclusion content and high performance stability.
In some embodiments of the present application, the yield strength R of the ultra high carbon steel sheet el ≥850MPa；
Optionally, tensile strength R of the ultra-high carbon steel sheet m ≥1250MPa；
Optionally, the elongation after fracture of the ultrahigh carbon steel plate is more than or equal to 8%.
In some embodiments, mechanical properties of the ultra-high carbon steel plate provided by some embodiments of the present application are detected, and the yield strength exceeds 850MPa, the tensile strength exceeds 1250MPa, and the elongation after fracture is more than 8%, which indicates that the ultra-high carbon steel plate has higher strength and certain toughness, and is beneficial to further processing and utilization of the ultra-high carbon steel plate.
In some embodiments of the present application, the thickness of the ultra-high carbon steel sheet is 1.5 to 3mm.
In a second aspect, the present application provides a method for manufacturing an ultra-high carbon steel plate based on a thin slab continuous casting and rolling process, comprising the following steps:
s10: performing converter smelting on the raw materials by using a slag-remaining double-slag method to obtain molten steel, wherein the content of C in the molten steel is more than 0.3 percent and the content of P in the molten steel is less than 0.01 percent in terms of mass fraction;
s20: adding a carburant and an alloy material into the molten steel and then refining to obtain alloyed molten steel with the chemical element composition of any one embodiment of the first aspect;
s30: and continuously casting the alloying molten steel to obtain a casting blank.
According to the technical scheme, the ultrahigh-carbon steel plate is manufactured based on a thin slab continuous casting and rolling process, the C content in molten steel obtained by smelting in a converter is controlled to be more than 0.3%, the P element is controlled to be less than 0.01%, the oxidability of the molten steel is controlled, deoxidation products are reduced, the cleanliness of the molten steel is improved, the addition amount of a carburant can be reduced, and alloyed molten steel with chemical element composition in the first aspect of embodiment is obtained through refining treatment, so that the number of inclusions in the ultrahigh-carbon steel plate is remarkably reduced, and the ultrahigh-carbon steel plate with high strength is obtained.
In the technical scheme of the application, in order to ensure that the content of C in molten steel is more than 0.3 percent and the content of P element is less than 0.01 percent, in the process of smelting the converter, temperature measurement, sampling and carbon determination (TSC) are carried out when the oxygen supply amount is 80-85 percent, and the end point carbon drawing and deep dephosphorization operation is carried out according to the TSC detection result.
In some embodiments of the present application, in step S10, the final slag basicity in converter smelting is 3 to 3.5.
In some embodiments, because the converter smelting is carried out by adopting the slag-remaining double-slag method, the higher alkalinity of the final slag is beneficial to dephosphorization, so that the dephosphorization amount required in the decarburization process is reduced, namely most phosphorus elements are removed in the dephosphorization stage, and the phosphorus content can not meet the requirement when the C content in molten steel is more than 0.3 percent.
In some embodiments of the present application, in the continuous casting process, the viscosity of the continuous casting mold flux is 0.012 to 0.13Pa · S, the melting temperature is 710 to 850 ℃, and the binary basicity is 0.8 to 1 in step S30.
In some of the above examples, generally speaking, the requirements of different steel grades for mold flux depend on the carbon content and alloy elements of the steel grades, and the properties of mold flux required by steel grades with different carbon contents are greatly different, mainly the requirements of lubricating property and heat transfer property are different. Because the liquidus of the ultra-high carbon steel plate is low, the solid-liquidus temperature difference is large, the molten steel fluidity is good, solute elements are easy to segregate, the effective thickness of a solidified blank shell can be reduced, and the thinner blank shell is tightly attached to the wall of a crystallizer under the action of the static pressure of the molten steel, so that large friction resistance is generated, and adhesion breakout are easy to generate; meanwhile, because the high-carbon steel has strong heat conduction capability, the blank shell grows quickly and is relatively uniform, and cracks and crack breakout are not easy to occur; comprehensively, the continuous casting covering slag required by the ultra-high carbon steel plate provided by the application needs to have the characteristics of low melting temperature, low crystallization temperature, good glass state, relatively low alkalinity and good lubricity. Therefore, the ultra-high carbon steel plate provided by the application uses the continuous casting covering slag with the viscosity of 0.012-0.13 Pa.s, the melting temperature of 710-850 ℃ and the binary alkalinity of 0.8-1, so that the covering slag has excellent fluidity after being melted, the lubrication function between the blank shell and the crystallizer is fully exerted, the bonding and the steel leakage are prevented, and the smooth continuous casting production is ensured. Wherein the binary alkalinity is the mass ratio of calcium oxide to silicon dioxide in the continuous casting mold flux.
In some embodiments of the present application, the continuous casting mold flux specifically includes: 12.5-16.5% by mass of Na 2 O，2％～4％Li 2 O，8.5％～15.5％F - ；
Preferably, the continuous casting mold flux specifically includes: 14.5 to 16 percent of Na by mass fraction 2 O，2％～3.5％Li 2 O，12％～14％F - 。
In some embodiments, the specific content of some components in the continuous casting mold flux is controlled to obtain the mold flux with low melting temperature, low crystallization temperature, good glass state and good lubricity, wherein compared with the continuous casting mold flux in the prior art, the melting temperature of the mold flux is reduced and the lubricity of the mold flux is improved by increasing the mass fractions of sodium oxide, lithium oxide and fluorine ions, so that the problems of bonding, steel leakage, cracks and the like are prevented.
In some embodiments of the present application, the continuous casting mold flux further includes: 16.2-26% of CaO, 18.9-26% of SiO in terms of mass fraction 2 。
In some of the above embodiments, calcium oxide and silicon dioxide are main components of the continuous casting mold flux, and the binary basicity of the continuous casting mold flux may be adjusted by adjusting the mass ratio therebetween to meet the continuous casting requirement.
In some embodiments of the present application, in the continuous casting process, the degree of superheat of the molten steel is 15 to 30 ℃.
In some embodiments, according to the mechanism of formation of isometric crystals of a casting blank, the lower the superheat degree of the molten steel, the smaller the proportion of columnar crystal regions, and the obvious growth orientation of the columnar crystals, the easy enrichment of solute elements among the columnar crystals to cause segregation, so that the superheat degree of the molten steel is not easy to be too high, but the too low superheat degree of the molten steel is not beneficial to melting of continuous casting mold flux, and the superheat degree of the molten steel is controlled to be 15-30 ℃ by combining the element composition and the actual production process of the ultra-high carbon steel plate provided by the application.
In some embodiments of the present application, in the continuous casting process, the continuous casting drawing speed is 3.5 to 4m/S, and the liquid core reduction is 5 to 10mm in step S30.
In some embodiments, if the continuous casting drawing speed is too high, a billet shell with enough thickness cannot be formed to support the ferrostatic pressure, and if the continuous casting drawing speed is too low, the risk of bonding breakout is increased, and the continuous casting drawing speed is controlled to be 3.5-4 m/s and the liquid core reduction is 5-10 mm by combining the element composition and the actual production process of the ultra-high carbon steel plate provided by the application.
In some embodiments of the present application, in the continuous casting process, the specific water amount of the continuous casting secondary cooling zone is 1.6 to 1.7L/(kg · min).
In some embodiments, because the ultrahigh-carbon steel plate has low high-temperature strength and high crack sensitivity, secondary cooling should be weakly controlled to improve the thermoplasticity of the casting blank in order to avoid cracks at the edge of the casting blank, and if the secondary cooling strength is higher, the surface temperature of the casting blank is lower, so that the temperature gradient on the cross section of the casting blank is increased, the proportion of columnar crystals is enlarged, element segregation is caused, and therefore the specific water content in the continuous casting secondary cooling area is not easily too high; however, if the secondary cooling strength is too low, solidification may be incomplete, and quality defects such as bulging of a casting blank, breakout and the like may be caused, so that the specific water amount in the continuous casting secondary cooling zone is controlled to be 1.6 to 1.7L/(kg · min) by combining the element composition of the ultra-high carbon steel plate provided by the present application and the actual production process.
In some embodiments of the present application, the method of manufacturing further comprises the steps of:
s40: and heating, dephosphorizing, rolling, cooling and coiling the casting blank to obtain the ultrahigh carbon steel plate.
In some embodiments, the casting blank needs to be further processed to obtain an ultra-high carbon steel plate for further utilization, and the ultra-high carbon steel plate with good performance can be obtained by using a conventional steel plate processing method.
In some embodiments of the present application, in the step S40, the charging temperature is 850-900 ℃ during the heating process;
optionally, in the rolling process, the final rolling temperature is 880-910 ℃;
optionally, in the coiling process, the coiling temperature is 650-680 ℃.
Hereinafter, the ultra-high carbon steel sheet material and the method for manufacturing the same according to the present invention will be described in more detail with reference to examples, but the scope of the present invention is not limited to these examples.
Example 1
The method for manufacturing the ultra-high carbon steel plate based on the thin slab continuous casting and rolling process comprises the following steps:
the process flow comprises the steps of converter smelting, ladle furnace refining, continuous slab casting, soaking, high-pressure water descaling, hot continuous rolling, laminar cooling and coiling of raw materials to obtain the ultra-high carbon steel plate.
S10: performing converter smelting on the raw materials by using a slag-remaining double-slag method to obtain molten steel, wherein the alkalinity of final slag is 3.2, and the mass fraction of the molten steel is as follows: 0.32%, P:0.008 percent.
S20: adding a recarburizing agent and an alloy material into the molten steel, and refining to obtain alloyed molten steel, wherein the alloy molten steel comprises the following components in percentage by mass: 1.23%, P:0.0095%, si:0.18%, mn:0.38%, S:0.003%, als:0.027%, the balance being Fe and unavoidable impurities.
S30: carrying out continuous casting treatment on the alloyed molten steel to obtain a casting blank, wherein the viscosity of the continuous casting covering slag is 0.1Pa & s, the melting temperature is 810 ℃, the binary alkalinity is 0.95, and the continuous casting covering slag specifically comprises the following components: 15.63% by mass of Na 2 O，2.81％Li 2 O，12.33％F - (ii) a The superheat degree of the molten steel is 21 ℃; the specific water amount of the continuous casting secondary cooling area is 1.68L/(kg & min); the continuous casting speed is 3.9m/s, the liquid core reduction is 5mm, and the thickness of the casting blank is 65mm.
S40: heating, dephosphorizing, rolling, cooling and coiling a casting blank to obtain an ultra-high carbon steel plate with the thickness of 1.8mm, wherein the charging temperature is 870 ℃ in the heating process; in the rolling process, the finishing temperature is 890 ℃; in the coiling process, the coiling temperature is 670 ℃.
Example 2
The method for manufacturing the ultra-high carbon steel plate based on the thin slab continuous casting and rolling process comprises the following steps:
the process flow comprises the steps of smelting raw materials by a converter, refining by a ladle furnace, continuously casting a plate blank, soaking, descaling by high-pressure water, hot continuous rolling, laminar cooling and coiling to obtain the ultra-high carbon steel plate.
S10: performing converter smelting on the raw materials by using a slag-remaining double-slag method to obtain molten steel, wherein the alkalinity of final slag is 3.1, and the mass fraction in the molten steel is C:0.31%, P:0.007%.
S20: adding a recarburizing agent and an alloy material into the molten steel, and refining to obtain alloyed molten steel, wherein the alloy molten steel comprises the following components in percentage by mass: 1.22%, P:0.01%, si:0.19%, mn:0.4%, S:0.002%, als:0.024 percent, and the balance being Fe and inevitable impurities.
S30: carrying out continuous casting treatment on the alloyed molten steel to obtain a casting blank, wherein the viscosity of the continuous casting covering slag is 0.09Pa & s, the melting temperature is 815 ℃, the binary alkalinity is 0.9, and the continuous casting covering slag specifically comprises: 15.2% by mass of Na 2 O，3.15％Li 2 O，12.56％F - (ii) a The superheat degree of the molten steel is 25 ℃; the specific water amount of the continuous casting secondary cooling area is 1.65L/(kg & min); the continuous casting speed is 3.8m/s, the liquid core reduction is 10mm, and the thickness of the casting blank is 60mm.
S40: heating, dephosphorizing, rolling, cooling and coiling the casting blank to obtain an ultrahigh carbon steel plate with the thickness of 2mm, wherein the charging temperature is 860 ℃ in the heating process; in the rolling process, the finishing temperature is 885 ℃; during the winding, the winding temperature was 675 ℃.
Example 3
The method for manufacturing the ultra-high carbon steel plate based on the thin slab continuous casting and rolling process comprises the following steps:
the process flow comprises the steps of converter smelting, ladle furnace refining, continuous slab casting, soaking, high-pressure water descaling, hot continuous rolling, laminar cooling and coiling of raw materials to obtain the ultra-high carbon steel plate.
S10: performing converter smelting on the raw materials by using a slag-remaining double-slag method to obtain molten steel, wherein the alkalinity of final slag is 3.3, and the mass fraction in the molten steel is C:0.34%, P:0.001 percent.
S20: adding a recarburizing agent and an alloy material into the molten steel, and refining to obtain alloyed molten steel, wherein the alloy molten steel comprises the following components in percentage by mass: 1.2%, P:0.011%, si:0.23%, mn:0.37%, S:0.0025%, als:0.03%, and the balance of Fe and inevitable impurities.
S30: carrying out continuous casting treatment on the alloyed molten steel to obtain a casting blank, wherein the viscosity of the continuous casting covering slag is 0.11Pa & s, the melting temperature is 800 ℃, the binary alkalinity is 0.92, and the continuous casting covering slag specifically comprises the following components: 14.71% by mass of Na 2 O，3.32％Li 2 O，12.83％F - (ii) a The superheat degree of the molten steel is 18 ℃; the specific water amount of the continuous casting secondary cooling area is 1.67L/(kg & min); the continuous casting speed is 3.8m/s, the liquid core reduction is 10mm, and the thickness of the casting blank is 60mm.
S40: heating, dephosphorizing, rolling, cooling and coiling the casting blank to obtain an ultrahigh carbon steel plate with the thickness of 2.5mm, wherein the charging temperature is 855 ℃ in the heating process; in the rolling process, the final rolling temperature is 880 ℃; during the coiling, the coiling temperature was 665 ℃.
Comparative example 1
The method for manufacturing the ultra-high carbon steel plate based on the thin slab continuous casting and rolling process comprises the following steps:
the process flow comprises the steps of smelting raw materials by a converter, refining by a ladle furnace, continuously casting a plate blank, soaking, descaling by high-pressure water, hot continuous rolling, laminar cooling and coiling to obtain the ultra-high carbon steel plate.
S10: performing converter smelting on the raw materials by using a slag-remaining double-slag method to obtain molten steel, wherein the alkalinity of final slag is 3.2, and the mass fraction of the molten steel is as follows: 0.25%, P:0.008 percent.
S20: adding a recarburizer and an alloy material into the molten steel, and then refining to obtain alloyed molten steel, wherein the alloyed molten steel comprises the following components in percentage by mass: 1.19%, P:0.0085%, si:0.25%, mn:0.35%, S:0.0021%, als:0.028%, and the balance of Fe and inevitable impurities.
S30: continuously casting the alloyed molten steel to obtain a casting blank, wherein the viscosity of the continuous casting covering slag is 0.1 Pa.s, the melting temperature is 820 ℃, the binary alkalinity is 0.88, and a concrete package of the continuous casting covering slagComprises the following steps: 15.43% by mass of Na 2 O，2.02％Li 2 O，13.15％F - (ii) a The superheat degree of the molten steel is 18 ℃; the specific water amount of the continuous casting secondary cooling area is 1.65L/(kg & min); the continuous casting speed is 3.6m/s, the liquid core reduction is 10mm, and the thickness of the casting blank is 60mm.
S40: heating, dephosphorizing, rolling, cooling and coiling a casting blank to obtain an ultra-high carbon steel plate with the thickness of 1.95mm, wherein the charging temperature is 855 ℃ in the heating process; in the rolling process, the final rolling temperature is 880 ℃; during the coiling, the coiling temperature was 665 ℃.
Test methods and results
The ultra-high carbon steel plate is sampled according to GB/T2975 sampling position and sample preparation of mechanical property test of steel and steel products.
(1) And (3) metallographic structure observation:
preparing a 4% nitric acid alcohol corrosion reagent, dripping 1-2 drops of the reagent on the surface of the ground ultrahigh carbon steel plate manufactured in the examples 1-3 and the comparative example 1, staying the surface of the sample for about 10s until the sample surface becomes dark from a mirror image, washing the sample surface with alcohol, quickly treating the sample surface on absorbent paper, and finally drying the sample surface by using an electric blower to determine the tissue type under a metallographic microscope.
The microstructure was observed by means of a Zeiss (ZEISS) metallographic microscope (OM). The measured tissue sample is placed above a Zeiss microscope lens, the focal length of the microscope is adjusted, the microscopic structure of the sample can be clearly shown on a computer, the microscope is properly adjusted, the position of the lens is properly moved up, down, left and right to observe the structure of the microscopic structure, the magnification is selected, photographing is carried out, the size is marked, and the microscopic structure is used as a test analysis research object in the future. The observation results are shown in fig. 1 to 4, wherein fig. 1 to 4 are metallographic structure diagrams of examples 1, 2 and 3 and comparative example 1, respectively.
As can be seen from the results of fig. 1 to 4, the metallographic structures of the ultra high carbon steel sheets prepared in examples 1 to 3 and comparative example 1 were mainly composed of pearlite and a small amount of cementite, and the ultra high carbon steel sheets thus obtained had good yield strength and tensile strength.
(2) Yield strength R of ultra-high carbon steel sheets manufactured in examples 1 to 3 and comparative example 1 according to GB/T228.1-2010 part 1 Room temperature test method of tensile test of Metal Material el Tensile strength R m And elongation after break a, the results are shown in table 1.
(3) And (3) detecting the Rockwell hardness difference of the quenched steel plate:
the results of the rockwell hardness differences after quenching of the ultra-high carbon steel sheets manufactured in examples 1 to 3 and comparative example 1 were measured according to GB/T230.1-2018 "metal rockwell hardness test" and are shown in table 1.
(4) The inclusions of the ultra-high carbon steel sheets manufactured in examples 1 to 3 and comparative example 1 were examined according to GB/T10561-2005 "microscopic examination method for measuring the content of nonmetallic inclusions in steel", and the results are shown in Table 1.
(5) The results of examining the decarburized layers of the ultra-high carbon steel sheets manufactured in examples 1 to 3 and comparative example 1 according to GB/T224-2008 "method for measuring depth of decarburized layer of Steel" are shown in Table 1.
TABLE 1
From the results shown in table 1, it is understood that the ultra-high carbon steel sheets having a thickness of 1.8 to 2.5mm and good coil shape, which were prepared in examples 1 to 3 of the present application, had a small number of inclusions and had good strength, yield strength R el Not less than 850MPa, tensile strength R m The tensile strength of the carbon is more than or equal to 1250MPa, the elongation A after fracture is more than or equal to 8 percent, and the ratio of the depth to the thickness of the decarburized layer is not more than 0.15 percent, so that the carbon has good quenching hardness and wear resistance, and can prevent deformation and cracks during heat treatment. Among them, the ultra-high carbon steel sheet of comparative example 1 had more inclusions and low elongation after fracture than those of examples, and it is possible that the reason is carbon in molten steel obtained by converter smeltingThe content is lower than 0.3%, the oxygen content of the molten steel is relatively high, more aluminum deoxidizing and carburant needs to be added to reach the target carbon content, and therefore more inclusions are introduced, so that the structure performance is uneven and the elongation after fracture is poor.
Finally, it should be noted that: the above embodiments are only used to illustrate the technical solutions of the present application, and not to limit the same; although the present application has been described in detail with reference to the foregoing embodiments, those of ordinary skill in the art will understand that: the technical solutions described in the foregoing embodiments may still be modified, or some or all of the technical features may be equivalently replaced; and these modifications or substitutions do not depart from the scope of the technical solutions of the embodiments of the present application.
Claims (10)
1. The ultrahigh carbon steel plate is characterized by comprising the following chemical elements in percentage by mass:
c:1.15% -1.5%, preferably 1.15% -1.25%;
si:0.1% -0.35%, preferably 0.1% -0.25%;
mn:0.1% -0.4%, preferably 0.3% -0.4%;
and Als:0.02 to 0.05%, preferably 0.02 to 0.03%;
p:0 to 0.03%, preferably 0 to 0.015%;
s:0 to 0.03%, preferably 0 to 0.004%;
the balance being Fe and unavoidable impurity elements.
2. The ultra-high carbon steel sheet as claimed in claim 1, wherein a ratio of a depth of a decarburized layer of the ultra-high carbon steel sheet to a thickness of the ultra-high carbon steel sheet is not more than 0.15%.
3. The ultra-high carbon steel sheet as claimed in claim 1, wherein the grade of B-type inclusions in the ultra-high carbon steel sheet is not more than 0.5; the grade of the D-type inclusion is less than or equal to 1.
4. The ultra-high carbon steel sheet as claimed in claim 1, wherein the difference in Rockwell hardness after quenching is not more than 2.2.
5. The ultra-high carbon steel sheet as claimed in claim 1, wherein the yield strength R of the ultra-high carbon steel sheet el ≥850MPa；
Optionally, the tensile strength R of the ultrahigh carbon steel plate m ≥1250MPa；
Optionally, the elongation after fracture of the ultrahigh carbon steel plate is more than or equal to 8%.
6. A method for manufacturing an ultra-high carbon steel plate based on a thin slab continuous casting and rolling process is characterized by comprising the following steps:
s10: performing converter smelting on the raw materials by using a slag-remaining double-slag method to obtain molten steel, wherein the content of C in the molten steel is more than 0.3 percent and the content of P in the molten steel is less than 0.01 percent in terms of mass fraction;
s20: adding a recarburizer and an alloy material to the molten steel and then refining the mixture to obtain alloyed molten steel with the chemical element composition according to claim 1;
s30: and continuously casting the alloying molten steel to obtain a casting blank.
7. The method according to claim 6, wherein in the step S30, the viscosity of the continuous casting mold flux is 0.012 to 0.13 Pa-S, the melting temperature is 710 to 850 ℃, and the basicity is 0.8 to 1 in the continuous casting process.
8. The method according to claim 7, wherein the continuous casting mold flux specifically includes: 12.5 to 16.5% by mass of Na 2 O，2％～4％Li 2 O，8.5％～15.5％F - ；
Preferably, the continuous casting mold flux specifically includes: 14.5 to 16% by mass of Na 2 O，2％～3.5％Li 2 O，12％～14％F - 。
9. The method according to claim 6, wherein in the step S30, the specific water amount in the continuous casting secondary cooling zone is 1.6-1.7L/(kg-min).
10. The method of claim 6, further comprising the steps of:
s40: and heating, dephosphorizing, rolling, cooling and coiling the casting blank to obtain the ultrahigh carbon steel plate.
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