CN111647733B - Method for improving phosphating performance of low-carbon aluminum killed steel automobile plate and automobile plate - Google Patents
Method for improving phosphating performance of low-carbon aluminum killed steel automobile plate and automobile plate Download PDFInfo
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- CN111647733B CN111647733B CN202010395272.1A CN202010395272A CN111647733B CN 111647733 B CN111647733 B CN 111647733B CN 202010395272 A CN202010395272 A CN 202010395272A CN 111647733 B CN111647733 B CN 111647733B
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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
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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Abstract
The invention specifically relates to a method for improving the phosphating performance of a low-carbon aluminum killed steel automobile plate and the automobile plate, relates to the field of steel smelting, and provides the method for improving the phosphating performance of the low-carbon aluminum killed steel automobile plate, which comprises the steps of casting blank component control, hot rolling, cold rolling, annealing and leveling; in the casting blank component control, the casting blank components are controlled according to the mass fraction: c: 0.01-0.02%, Si is less than or equal to 0.02%, Mn: 0.10-0.30%, P is less than or equal to 0.015%, S is less than or equal to 0.015%, Al: 0.03-0.06%, B: 0.001-0.003%, N is less than or equal to 0.005%, and the balance is Fe and inevitable impurities; in the hot rolling, the temperature of a steel billet is 1140-1240 ℃, the outlet temperature of rough rolling is 1020-1100 ℃, and the finishing temperature is 900-960 ℃; in the cold rolling, the cold rolling reduction is 67.6-86.1%; in the annealing, the dew point temperature of the heating section of the annealing furnace is-30-0 ℃. The low-carbon aluminum killed steel automobile plate prepared by the method provided by the embodiment of the invention has the advantages that the grain size of a phosphating film on the surface is less than 5um, the coverage rate is 100 percent, the P ratio is more than 85 percent, and the low-carbon aluminum killed steel automobile plate has excellent phosphating performance.
Description
Technical Field
The invention relates to the field of steel smelting, in particular to a method for improving the phosphating performance of a low-carbon aluminum killed steel automobile plate and the automobile plate.
Background
Phosphating is a process in which chemical and electrochemical reactions form a phosphate chemical conversion coating, which is referred to as a phosphating coating. The purpose of the phosphorization mainly comprises the following aspects: 1) the base metal is protected, and the metal is prevented from being corroded to a certain extent; 2) the primer is used for priming before painting, and the adhesive force and the corrosion resistance of a paint film layer are improved; 3) the lubricant is used for antifriction and lubrication in a metal cold working process.
At present, the problem of insufficient phosphating performance exists in low-carbon aluminum killed steel automobile plates.
Disclosure of Invention
In view of the above problems, the present invention has been made to provide a method for improving the phosphatability of low carbon aluminum killed steel automotive sheet, an automotive sheet, which overcomes or at least partially solves the above problems.
The embodiment of the invention provides a method for improving the phosphating performance of a low-carbon aluminum killed steel automobile plate, which comprises the steps of casting blank component control, hot rolling, cold rolling, annealing and leveling;
in the casting blank component control, the casting blank components are controlled according to the mass fraction: c: 0.01-0.02%, Si is less than or equal to 0.02%, Mn: 0.10-0.30%, P is less than or equal to 0.015%, S is less than or equal to 0.015%, Al: 0.03-0.06%, B: 0.001-0.003%, N is less than or equal to 0.005%, and the balance is Fe and inevitable impurities;
in the hot rolling, the temperature of a steel billet is 1140-1240 ℃, the outlet temperature of rough rolling is 1020-1100 ℃, and the finishing temperature is 900-960 ℃;
in the cold rolling, the cold rolling reduction is 67.6-86.1%;
in the annealing, the dew point temperature of the heating section of the annealing furnace is-30-0 ℃.
Optionally, in the hot rolling, the curling temperature is 640-700 ℃.
Optionally, in the annealing, the dew point temperatures of the preheating section, the soaking section and the cooling section of the annealing furnace are all less than or equal to-45 ℃.
Optionally, in the annealing, the oxygen mass content and H of the preheating section, the heating section, the soaking section and the cooling section of the annealing furnace2The mass content satisfies: oxygen content less than or equal to 15ppm, H2The mass content is less than or equal to 7 percent.
Optionally, in the leveling, the steel plate is leveled until the Ra value of the surface of the steel plate is 1.0-1.4 um, and the RPc is more than or equal to 90.
Optionally, the mass fraction ratio of the Mn to the Si is 10-15.
Optionally, the steel tapping billet temperature is 1200 ℃, the rough rolling outlet temperature is 1050 ℃, and the finish rolling temperature is 910 ℃.
Optionally, the cold rolling reduction is 82.5%.
Optionally, the dew point temperature of the heating section of the annealing furnace is-20 ℃.
Based on the same invention concept, the embodiment of the invention also provides a low-carbon aluminum killed steel automobile plate which is prepared by the method for improving the phosphating performance of the low-carbon aluminum killed steel automobile plate.
One or more technical solutions in the embodiments of the present invention have at least the following technical effects or advantages:
according to the method for improving the phosphating performance of the low-carbon aluminum killed steel automobile plate, provided by the embodiment of the invention, through casting blank component control, hot rolling, cold rolling and annealing, oxide particles formed on the surface of the steel plate are smaller and are distributed in a dispersed manner, and through leveling process control, the number of concave-convex fluctuation structures on the surface of the steel plate is increased, so that the surface quality of the steel plate is improved, and the phosphating performance requirement of the steel plate under the lower limit condition of a phosphating process is met.
The steel plate (automobile plate) for the automobile, which is prepared by the method for improving the phosphating performance of the low-carbon aluminum killed steel automobile plate, provided by the embodiment of the invention, has the surface phosphating film with the grain size of below 5um, the coverage rate of 100 percent and the P ratio of more than 85 percent.
The foregoing description is only an overview of the technical solutions of the present invention, and the embodiments of the present invention are described below in order to make the technical means of the present invention more clearly understood and to make the above and other objects, features, and advantages of the present invention more clearly understandable.
Drawings
Various other advantages and benefits will become apparent to those of ordinary skill in the art upon reading the following detailed description of the preferred embodiments. The drawings are only for purposes of illustrating the preferred embodiments and are not to be construed as limiting the invention. Also, like reference numerals are used to refer to like parts throughout the drawings. In the drawings:
FIG. 1 is a map of the surface appearance of a phosphating film on a low-carbon aluminum killed steel automobile plate in example 1 of the invention;
FIG. 2 is a map of the appearance of the phosphating coatings on the surfaces of the low-carbon aluminum killed steel automobile plates in the embodiment 2 of the invention.
Detailed Description
The present invention will be described in detail below with reference to specific embodiments and examples, and the advantages and various effects of the present invention will be more clearly apparent therefrom. It will be understood by those skilled in the art that these specific embodiments and examples are for the purpose of illustrating the invention and are not to be construed as limiting the invention.
Throughout the specification, unless otherwise specifically noted, terms used herein should be understood as having meanings as commonly used in the art. Accordingly, unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. If there is a conflict, the present specification will control.
Unless otherwise specifically stated, various raw materials, reagents, instruments, equipment and the like used in the present invention are commercially available or can be prepared by existing methods.
It should be further noted that 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.
As previously mentioned, currently, low carbon aluminum killed steel automotive panels suffer from insufficient phosphatization properties for reasons including:
1. surface roughness. The influence of the surface roughness of the steel plate on the phosphating performance is large, and the fluctuation size and the fluctuation quantity of the surface structure of the material are different mainly due to different roughness, so that the effective reaction areas of the material in the phosphating solution are different, the nucleation rate of the material is different, and the final phosphating performance of the material is different. Characteristic parameters in surface roughness such as Ra (arithmetic mean deviation of profile), RPc (peak density of waviness), etc. all have an influence on the phosphating performance.
2. Surface oxide aggregate state. The automobile plate is generally an annealing plate, and in the annealing process, because the protective atmosphere in the annealing furnace has certain oxidizability, alloy elements of the material are selectively oxidized to form oxides. The different components and contents of the material and the difference of annealing system cause the different types and forms of the oxides on the surface of the material, and the influence on the phosphating performance is different. In general, selective oxidation of the surface of a material generally has a beneficial effect on phosphating performance if it forms a relatively fine, particulate, uniformly distributed oxide. If the size of the oxide is large, the distribution is not uniform, or the oxide directly exists in a film-like form, the phosphating performance is extremely unfavorable.
3. Surface residual oil and carbon, and the like. The carbon residue on the surface of the material can cause the adverse effects of rough phosphorization crystal, weakened corrosion resistance of a matching coating and the like. When the amount of residual oil on the surface of the material is large, the burden of degreasing is increased, and poor phosphatization may also be caused.
In order to solve the technical problems, the technical scheme in the embodiment of the invention has the following general idea:
the embodiment of the invention provides a method for improving the phosphating performance of a low-carbon aluminum killed steel automobile plate, which comprises the steps of casting blank component control, hot rolling, cold rolling, annealing and leveling;
in the casting blank component control, the casting blank components are controlled according to the mass fraction: c: 0.01-0.02%, Si is less than or equal to 0.02%, Mn: 0.10-0.30%, P is less than or equal to 0.015%, S is less than or equal to 0.015%, Al: 0.03-0.06%, B: 0.001-0.003%, N is less than or equal to 0.005%, and the balance is Fe and inevitable impurities;
in the hot rolling, the temperature of a steel billet is 1140-1240 ℃, the outlet temperature of rough rolling is 1020-1100 ℃, and the finishing temperature is 900-960 ℃;
in the cold rolling, the cold rolling reduction is 67.6-86.1%;
in the annealing, the dew point temperature of the heating section of the annealing furnace is-30-0 ℃.
1. By utilizing the scheme, the oxides which are distributed dispersedly and have small size can be formed on the surface of the steel plate, and the number of the concave-convex fluctuation structures on the surface of the steel plate is large and uniform, so that the surface of the steel plate can react quickly under the condition of the lower limit phosphating process, the phosphating nucleation rate is increased, and a phosphating film with good quality can be formed.
2. The components of the casting blank are controlled mainly to ensure the mechanical property, the stamping property and the like of the steel plate, avoid the occurrence of blocky carbides at the crystal boundary of the steel plate and promote the surface of the steel plate to form fine and dispersed Fe3C, so as to improve the phosphating performance of the steel plate. The hot rolling process is controlled mainly to ensure the mechanical property and the surface quality of the steel plate and achieve the aim of saving energy. The cold rolling reduction rate of the steel plate is controlled, and the better stamping performance is mainly obtained. The dew point of the heating section of the annealing furnace is controlled, and the dew point is mainly used for forming dispersed small-size oxides on the surface of the steel plate so as to improve the phosphating performance of the steel plate.
3. The range of controlling the composition of the cast slab of the present invention will be described.
C：0.01％-0.02％
C is the most basic solid solution strengthening element of the steel plate, and can effectively improve the strength of the steel plate. However, the content of C element is too high, a large amount of carbide can be formed, the phosphating performance is not good, and the smelting difficulty and the cost are increased, so that the content of C element in the invention is controlled to be 0.01-0.02%.
Si：≤0.02％
The Si element content is too high, the Si element is easy to be enriched on the surface of the steel plate, a film-shaped or large-size Si-containing oxide which is easy to be aggregated in a grain boundary is formed, and the oxide is unfavorable for phosphorization nucleation, so that the phosphorization performance is poor, and therefore, the Si element content is controlled to be less than or equal to 0.02 percent.
Mn：0.10～0.30％
The Mn element can effectively increase the dispersion degree of oxides on the surface of the steel plate, reduce the size of the oxides and improve the phosphating performance of the steel plate, but the Mn element content is too high and the Mn segregation degree is increased, so that the Mn element content is controlled to be 0.10-0.30%.
P：≤0.015％
The P element is one of the basic elements of the steel plate, and the cold brittleness phenomenon can be caused by the high content of the P element, so the content of the P element is controlled to be less than or equal to 0.015 percent.
S：≤0.015％
The S element is one of the basic elements of the steel plate, and the high content can cause the phenomenon of hot brittleness, so the content of the S element is controlled to be less than or equal to 0.015 percent.
Al：0.03～0.06％
Al plays a role in deoxidation in molten steel smelting, the content is too low, the deoxidation is insufficient, but the smelting cost is increased if the content is too high, so that the AI element content is controlled to be less than or equal to 0.03-0.06%.
B：0.001～0.003％
The B element can play a quenching role, but the content is too high, so that the phosphating performance is not favorable, and therefore, the content of the B element is controlled to be 0.001-0.003%.
N：≤0.005％
The N element can improve the strength and the welding performance of the steel plate, so the content of the N element is controlled to be less than or equal to 0.005 percent.
3. The hot rolling process control of the present invention will be explained.
Hot rolling: the steel tapping billet temperature is 1140-1240 ℃, the rough rolling outlet temperature is 1020-1100 ℃, and the final rolling temperature is 900-960 ℃.
The steel billet temperature, the rough rolling outlet temperature and the final rolling temperature are controlled within the ranges, so that energy can be saved, decarburization can be reduced, the grain size can be controlled, and steel with uniform structure and stable performance can be obtained. Meanwhile, the scale of the steel plate is easy to clean within the range of the hot rolling process.
The cold rolling reduction is 67.6-86.1%, and if the cold rolling reduction is less than 67.6% or more than 86.1%, the steel sheet cannot obtain proper stamping performance.
The dew point temperature of the heating section of the annealing furnace is-30-0 ℃. If the dew point temperature is lower than-30 ℃ or higher than 0 ℃, the surface of the steel sheet cannot form dispersedly distributed oxides with small sizes or the oxidation degree is too severe.
Optionally, in the hot rolling, the curling temperature is 640-700 ℃.
The curling temperature is limited within the range, so that ideal metallographic structure and mechanical property can be obtained, the yield ratio can also reach the optimal value, and meanwhile, a better surface iron scale state can also be obtained.
Optionally, in the annealing, the dew point temperatures of the preheating section, the soaking section and the cooling section of the annealing furnace are all less than or equal to-45 ℃.
The dew point temperatures of the preheating section, the soaking section and the cooling section of the annealing furnace are limited to be less than or equal to minus 45 ℃ so as to ensure that the protective atmosphere in annealing presents a certain degree of reducibility and avoid overlarge oxidation degree of the steel plate.
Optionally, in the annealing, the oxygen mass content and H of the preheating section, the heating section, the soaking section and the cooling section of the annealing furnace2The mass content satisfies: oxygen content less than or equal to 15ppm, H2The mass content is less than or equal to 7 percent.
Limiting the oxygen mass content and H2The mass content is to avoid excessive oxidation of the steel sheet.
Optionally, in the leveling, the steel plate is leveled until the Ra value of the surface of the steel plate is 1.0-1.4 um, and the RPc is more than or equal to 90.
When the surface roughness characteristic value Ra and the RPc of the steel plate are limited in the range, a large number of 'concave-convex' undulating structures which are uniformly distributed can be obtained on the surface, and the phosphating performance is facilitated.
Optionally, the mass fraction ratio of the Mn to the Si is 10-15.
When the mass fraction ratio of Mn to Si of the steel plate is limited within the range, the enrichment degree of Mn elements on the surface of the steel plate can be increased, the enrichment degree of Si elements is reduced, oxides which are small in size and easy to dissolve in phosphating solution can be promoted to form on the surface of the steel plate, and the quality of a finally formed phosphating film is good.
Optionally, the steel tapping billet temperature is 1200 ℃, the rough rolling outlet temperature is 1050 ℃, and the finish rolling temperature is 910 ℃.
Optionally, the cold rolling reduction is 82.5%.
Optionally, the dew point temperature of the heating section of the annealing furnace is-20 ℃.
Based on the same invention concept, the embodiment of the invention also provides a low-carbon aluminum killed steel automobile plate which is prepared by the method for improving the phosphating performance of the low-carbon aluminum killed steel automobile plate.
The low-carbon aluminum killed steel automobile plate provided by the embodiment of the invention has the advantages that the grain size of a surface phosphating film is less than 5um, the coverage rate is 100%, the P ratio is more than 85%, and the low-carbon aluminum killed steel automobile plate has excellent phosphating performance.
The method for improving the phosphating performance of the low-carbon aluminum killed steel automobile plate and the automobile plate provided by the embodiment of the invention are explained in detail by combining the embodiment and experimental data.
Example 1
In this example, the composition of the cast slab was controlled as shown in table 1:
TABLE 1
| C | Si | Mn | P | S | Al | B | N |
| 0.0193 | 0.010 | 0.194 | 0.009 | 0.006 | 0.039 | 0.002 | 0.003 |
The steel tapping billet temperature is 1190 ℃, the rough rolling outlet temperature is 1045 ℃, the finish rolling temperature is 915 ℃ and the curling temperature is 680 ℃.
The cold rolling reduction was 67.6%.
The continuous annealing process is controlled as follows: the dew point of a heating section in the furnace is-25 ℃, and the dew point of the other sections is-46 ℃; the content of 0 in each stage is 10 ppm; the H2 content was 5%.
The flattening process is controlled as follows: the Ra value of the surface of the steel plate after leveling is 1.2um, and the RPc value is 93.
The topography of the phosphating film on the surface of the low-carbon aluminum killed steel automobile plate prepared by the embodiment is shown in fig. 1, and as can be seen from fig. 1, the phosphating film provided by the embodiment has uniform and compact crystallization, the grain size is below 5um, the coverage rate is 100 percent, and the P ratio is above 85 percent.
Example 2
In this example, the composition of the cast slab was controlled as shown in table 2:
TABLE 2
| C | Si | Mn | P | S | Al | B | N |
| 0.0190 | 0.013 | 0.199 | 0.006 | 0.005 | 0.043 | 0.003 | 0.003 |
The steel tapping billet temperature is 1180 ℃, the rough rolling outlet temperature is 1040 ℃, the finish rolling temperature is 910 ℃, and the curling temperature is 685 ℃.
The cold rolling reduction was 86.0%.
The continuous annealing process is controlled as follows: the dew point of the heating section in the furnace is-22 ℃, and the dew points of the other sections are-49 ℃; the content of 0 in each stage is 13 ppm; the H2 content was 7%.
The flattening process is controlled as follows: the Ra value of the surface of the steel plate after flattening is 1.3um, and the RPc is 116.
The topography of the phosphating film on the surface of the low-carbon aluminum killed steel automobile plate prepared by the embodiment is shown in fig. 2, and as can be seen from fig. 2, the phosphating film provided by the embodiment has uniform and compact crystallization, the grain size is below 5um, the coverage rate is 100 percent, and the P ratio is above 85 percent.
While preferred embodiments of the present invention have been described, additional variations and modifications in those embodiments may occur to those skilled in the art once they learn of the basic inventive concepts. Therefore, it is intended that the appended claims be interpreted as including preferred embodiments and all such alterations and modifications as fall within the scope of the invention.
It will be apparent to those skilled in the art that various changes and modifications may be made in the present invention without departing from the spirit and scope of the invention. Thus, if such modifications and variations of the present invention fall within the scope of the claims of the present invention and their equivalents, the present invention is also intended to include such modifications and variations.
Claims (5)
1. A method for improving the phosphating performance of a low-carbon aluminum killed steel automobile plate is characterized by comprising the steps of casting blank component control, hot rolling, cold rolling, annealing and leveling;
in the casting blank component control, the casting blank components are controlled according to the mass fraction: c: 0.01-0.02%, Si is less than or equal to 0.02%, Mn: 0.10-0.30%, P is less than or equal to 0.015%, S is less than or equal to 0.015%, Al: 0.03-0.06%, B: 0.001-0.003%, N is less than or equal to 0.005%, the mass fraction ratio of Mn to Si is 10-15, and the balance is Fe and inevitable impurities;
in the hot rolling, the temperature of a steel billet is 1140-1240 ℃, the outlet temperature of rough rolling is 1020-1100 ℃, and the finishing temperature is 900-960 ℃;
in the cold rolling, the cold rolling reduction is 67.6-86.1%;
in the annealing, the dew point temperature of a heating section of the annealing furnace is-30-0 ℃;
in the hot rolling, the curling temperature is 640-700 ℃;
in the annealing, the dew point temperatures of a preheating section, a soaking section and a cooling section of the annealing furnace are all less than or equal to minus 45 ℃;
in the annealing, the oxygen mass content and H of the preheating section, the heating section, the soaking section and the cooling section of the annealing furnace2The mass content satisfies: oxygen content less than or equal to 15ppm, H2The mass content is less than or equal to 7 percent;
in the leveling process, the steel plate is leveled until the Ra value of the surface of the steel plate is 1.0-1.4 um, and the RPc is more than or equal to 90.
2. The method for improving the phosphating performance of low-carbon aluminum killed steel automobile plates as claimed in claim 1, wherein the tapping steel billet temperature is 1200 ℃, the rough rolling outlet temperature is 1050 ℃, and the finish rolling temperature is 910 ℃.
3. The method for improving the phosphating performance of low-carbon aluminum killed steel automobile plates as claimed in claim 1, wherein the cold rolling reduction is 82.5%.
4. The method for improving the phosphating performance of the low-carbon aluminum killed steel automobile plate as claimed in claim 1, wherein the dew point temperature of a heating section of the annealing furnace is-20 ℃.
5. A low carbon aluminum killed steel automotive sheet, characterized by being produced by the method for improving phosphating properties of a low carbon aluminum killed steel automotive sheet as claimed in any one of claims 1 to 4;
the grain size of the surface phosphating film is less than 5um, the coverage rate is 100 percent, and the P ratio is more than 85 percent.
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| JP5609494B2 (en) * | 2010-09-29 | 2014-10-22 | Ｊｆｅスチール株式会社 | High strength steel plate and manufacturing method thereof |
| CA2811489C (en) * | 2010-09-30 | 2016-11-22 | Jfe Steel Corporation | High strength steel sheet and method for manufacturing the same |
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