CN115198184A - Rare earth hot rolled steel plate for 310 MPa-grade double-sided enamel after enamel and manufacturing method thereof - Google Patents
Rare earth hot rolled steel plate for 310 MPa-grade double-sided enamel after enamel and manufacturing method thereof Download PDFInfo
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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
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
Abstract
The invention relates to a rare earth hot rolled steel plate for 310 MPa-grade double-sided enamel after enamel and a manufacturing method thereof, wherein the steel comprises the following chemical components in percentage by weight: 0.031-0.049% of C, less than or equal to 0.10% of Si, 0.71-0.91% of Mn, 0.065-0.085% of P, 0.012-0.029% of S, 0.66-0.86% of Cr, 0.15-0.18% of Ti, 0.015-0.045% of Als, 0.0061-0.0079% of N, 0.051-0.071% of Sb, 0.0015-0.0029% of RE, and the balance of Fe and inevitable impurities. The advantages are that: the yield strength after enameling can reach over 310MPa, noble metal elements such as Nb, V, mo and the like do not need to be added, and the economy is good.
Description
Technical Field
The invention belongs to the technical field of low-alloy hot rolled steel plate production, and particularly relates to a rare earth hot rolled steel plate for 310 MPa-level double-sided enamel with excellent enameling performance and a manufacturing method thereof.
Background
Enamel products taking steel plates as metal substrates are closely related to people in daily life, and are widely applied to industries such as household appliances, metallurgy, chemical industry, buildings and the like to manufacture kitchen utensils, barbecue ovens, water heater liners, sanitary wares, building veneers, assembled reaction tanks and the like. With the increasing requirements for environmental protection in China, large-scale water treatment plant equipment, environmental protection facilities, large storage tanks and the like used in cities are becoming more popular, and high-strength hot-rolled steel plates serving as substrates are required to have high strength after high-temperature enameling, to allow double-sided enameling and to have good fishscale resistance.
In the prior art, patent application No.: 201710182661.4 discloses a 310 MPa-grade hot-rolled double-sided enameled steel and a manufacturing method thereof, wherein a Nb and Ti composite micro-alloying design is adopted, cr and Cu are added simultaneously, the addition of Cu is beneficial to surface deposition, and further the adhesion performance between the steel and enamel is improved, but Cu is generally added together with Ni, the surface of a steel plate added independently is easy to crack, and the requirement on a hot rolling process is strict. In addition, the addition of Nb is expensive. Patent application No.: 201510548170.8 discloses a hot rolled steel plate for high-strength double-sided enamel after enameling and a manufacturing method thereof, which adopts a composite micro-alloying design of Nb, V and Ti, and simultaneously selectively adds B elements, wherein the Nb and V elements are expensive and have high production cost. Patent application No.: 201710387916.0 discloses high-strength steel for hot rolling double-sided enamel, double-sided enamel steel and a manufacturing method thereof, the high-strength steel and the double-sided enamel steel have high C content, although the high-strength steel is effective for improving the strength after the enamel, the high C content easily causes air hole defects after the enamel is enameled. And the composite microalloying of Nb, V and Ti is adopted, so the cost is higher. Patent application No.: 200510047758.1 discloses a hot-rolled double-sided enameled steel plate and a manufacturing method thereof, wherein a Ti and V composite micro-alloying design is adopted, and the strength after enameling can not be ensured to be more than 310MPa, so that the use requirement of a user can not be completely met. The above patents are mainly designed by increasing the content of C or by using composite microalloying components of Nb, V and Ti to improve the strength of the steel sheet after the lining. Therefore, how to obtain a high-strength steel plate with excellent enameling performance by adopting low-cost component design is one of the technical difficulties to be solved urgently in the field.
Disclosure of Invention
In order to overcome the defects of the prior art, the invention aims to provide the rare earth hot-rolled steel plate for the 310 MPa-grade double-sided enamel and the manufacturing method thereof, which solve the problems of insufficient strength or high production cost of the hot-rolled double-sided enamel steel plate, have good fish scaling resistance, good adherence, no pinhole defect and high strength, and are suitable for manufacturing large assembled reaction tanks.
In order to realize the purpose, the invention is realized by the following technical scheme:
a rare earth hot rolled steel plate for 310 MPa-grade double-sided enamel after enamel is prepared from the following chemical components in percentage by weight: 0.031-0.049% of C, less than or equal to 0.10% of Si, 0.71-0.91% of Mn, 0.065-0.085% of P, 0.012-0.029% of S, 0.66-0.86% of Cr, 0.15-0.18% of Ti, 0.015-0.045% of Als, 0.0061-0.0079% of N, 0.051-0.071% of Sb0.0015-0.0029% of RE, and the balance of Fe and inevitable impurities.
The thickness of the steel plate is 3-12 mm, the yield strength is more than 510MPa, the tensile strength is more than 600MPa, and the elongation is more than 21%.
The reasons for selecting the above alloy element types and contents are as follows:
c is a key element for obtaining high strength of the steel plate and is the most economical element, but when the content of C is too high, the probability of generating pinhole defects after the enameling firing is higher. The content of C in the invention is limited to 0.031% -0.049%.
Si can be dissolved in ferrite and austenite to improve the hardness and strength of steel, but if the content is too high, red iron scale on the surface of a rolled steel plate is difficult to remove seriously, thereby affecting the adhesion of the steel plate. The content of Si is limited to not more than 0.10% in the present invention.
The main role of Mn in steel is solid solution strengthening, which acts to improve the strength of the steel sheet. The transformation temperature of austenite to ferrite can be obviously reduced, the microstructure of steel is refined, the strength index of a steel plate is ensured, but the plasticity of the steel is seriously reduced due to excessive Mn content, and the content of Mn is controlled to be 0.71-0.91%.
P has good solid solution strengthening effect and has no adverse effect on enamel performance. In the invention, P is used for compensating the insufficient solid solution strengthening caused by the reduction of C, but the content of P is too high, so that center segregation is easy to occur, the continuous casting billet is layered, and the mechanical property of the steel plate in the thickness direction is adversely affected, so that the content of P is controlled to be 0.065-0.085%.
S is an impurity element in steel, the ductility and the welding performance are obviously reduced, in the steel without titanium, sulfur is usually combined with manganese to form MnS inclusions, but in the invention, because of adding higher content of titanium, sulfur preferentially forms a compound with titanium, a certain hydrogen storage effect can be achieved, and the fish scaling resistance of the steel plate is improved. The content of the steel is controlled to be 0.012-0.029%.
Cr is beneficial to surface deposition, so that the adherence between the Cr and porcelain glaze is improved, the scaling resistance is improved, and meanwhile, the Cr has a certain solid solution strengthening effect and improves the strength of ferrite. The content range of the invention is limited to 0.66-0.86%.
Sb is usually present in the steel as a harmful element, and a suitable amount of Sb may be present in the steel during the production thereofSurface enrichment of (1) and inhibition of Fe to H in high-temperature enameling burning process 2 The reduction of O reduces the sources of H atoms dissolved in steel, reduces the enrichment of hydrogen between a porcelain layer and a steel interface, and is favorable for avoiding pinhole defects and reducing the risk of scale explosion. The content range of the invention is limited to 0.051-0.071%.
Ti is a strong carbonitride forming element, is an important microalloy strengthening element in the invention, not only can effectively refine grains, but also can form fine carbide, nitride or carbonitride with C, N and S, not only can strengthen the strength of a matrix, but also can provide a hydrogen trap and inhibit the occurrence of scale explosion after enameling firing. The invention is limited to the range of 0.15% to 0.18%.
Als is a commonly used deoxidizer, and the range of the deoxidizer is 0.015 to 0.045 percent.
RE can refine impurities in steel, reduce segregation of harmful elements in grain boundaries, interact with low-melting-point impurities such as phosphorus and antimony to form high-melting-point compounds, and inhibit segregation of the impurities on the grain boundaries. The rare earth has hydrogen trapping property, and the fish scaling resistance of the steel is improved. The invention limits the range to 0.0015% -0.0029%.
N is an element existing in the smelting process, and because one of the characteristics of the invention is to adopt Ti microalloying technology, and Ti is an element with strong activity, the Ti reacts with elements such as O, N, S and the like in steel, if the content of N is too high, tiN with large size can be separated out in molten steel, austenite grains can not be prevented from growing, the precipitation strengthening effect can not be achieved, and on the contrary, the refined grains of Ti and the precipitation strengthening effect can be reduced. Therefore, the range of N control in the invention is 0.0061% -0.0079%.
A manufacturing method of a rare earth hot rolled steel plate for 310 MPa-grade double-sided enamel after enamel, which comprises the following process routes: pre-desulfurizing molten steel, performing composite blowing at the top and the bottom of a converter, performing LF external refining, continuously casting a plate blank, heating the plate blank, performing hot continuous rolling, performing laminar cooling and coiling; the method specifically comprises the following steps:
1) The thickness of the casting blank is 200-230 mm; when the slab is heated, controlling the tapping temperature of a casting blank to be 1252-1281 ℃;
2) The hot continuous rolling adopts two-stage controlled rolling, each pass of rough rolling is descaled, and the outlet temperature of the rough rolling is more than 1100 ℃; the initial rolling temperature of finish rolling is 1081-1099 ℃, and the final rolling temperature of finish rolling is 911-935 ℃;
3) After finish rolling, laminar cooling is carried out, the steel is cooled to 619 to 649 ℃ at the cooling rate of 21 to 39 ℃/s, and then the steel is cooled to room temperature by air.
The laminar cooling adopts front section centralized cooling.
The process parameter selection reason in the manufacturing process of the rare earth hot rolled steel plate for 310MPa grade double-sided enamel after enamel is as follows:
(1) Heating the continuous casting billet at the temperature of 1252-1281 ℃; because the invention adds Ti with higher content, and Ti can combine with C and N to form stable carbide and nitride, the solid solution temperature is higher, in order to ensure that Ti can disperse and precipitate fine TiC in the rolling process and play a role of strong precipitation strengthening, the solid solution quantity of titanium carbide and titanium nitride is required to be ensured, and simultaneously, the soaking temperature is determined to be 1252-1281 ℃ in combination of the two aspects in consideration of the inhibition effect of the titanium carbide and the titanium nitride on the growth of original austenite grains.
(2) Rough rolling is carried out in the temperature range higher than 1100 ℃, band steel is not allowed to swing, finish rolling is started at 1081-1099 ℃, the start rolling temperature of finish rolling is higher than 1099 ℃, crystal grains of finished products are not easy to refine, and the fine grain strengthening effect is poor; the temperature of the tail part of the strip steel is quickly reduced below 1081 ℃, so that the load of a finish rolling machine frame is increased, and accidents are easily caused;
(3) When the finish rolling temperature is lower, the method is beneficial to the refinement of ferrite grain size and the improvement of fine-grain strengthening effect, but simultaneously, the lower finish rolling temperature can induce the deformation induced precipitation of the carbonitride. Although the precipitates inhibit the growth of austenite grains and perform certain functions of fine grain strengthening and precipitation strengthening, the precipitates are relatively large in size compared with ferrite-precipitated nano-scale particles, and the precipitation strengthening effect is reduced. Therefore, the finishing temperature of the invention is preferably controlled to be between 911 and 935 ℃.
(4) And after rolling, carrying out laminar cooling and coiling. The laminar flow adopts anterior segment centralized cooling, adopts anterior segment centralized cooling's purpose: firstly, crystal grains are refined, and the strength is improved; and secondly, the advance precipitation of TiC in the water cooling process is inhibited, so that Ti and C which are dissolved in the matrix are formed in the coiling process as much as possible, and the TiC has a strong precipitation strengthening effect. When the cooling rate is too low, ti carbide precipitates during cooling, coarse particles increase in the final product, the precipitation strengthening effect after coiling is insufficient, and the cooling rate is set to 21 to 39 ℃/s in order to ensure that a large amount of fine precipitated particles of the second phase are obtained after coiling. The coiling temperature is too high, the precipitation obtained after coiling is relatively thick, and the precipitation strengthening effect is weak; when the coiling temperature is too low, precipitation of precipitates becomes insufficient, and a desired strength cannot be obtained. Therefore, the coiling temperature of the present invention is preferably controlled to be 619-649 ℃.
The yield strength, the tensile strength and the elongation of the double-sided enameled pressed steel produced by the steel plate are all larger than 310MPa, 410MPa and 31 percent respectively; and the results of the fish scale explosion resistance performance test are that the fish scale explosion is not generated, the adherence performance is excellent and reaches grade 1, and no pinhole defect exists.
In the firing process of the enameled 310MPa grade double-sided enameled steel plate: enameling and burning the base glaze at 870-880 ℃ for 9-18min; the enameling burning temperature of the surface glaze is 780-800 ℃, and the enameling burning time is 7.5-15min.
Compared with the prior art, the invention has the beneficial effects that:
the rare earth hot rolled steel plate for 310MPa grade double-sided enamel after enameling is designed by adopting alloy components of high Ti, mn, cr and P solid solution strengthening elements and alloy elements Sb and RE, and forms a certain amount of TiN and Ti through the synergistic effect of the Mn, cr and P elements 4 S 2 C 2 And TiC, thereby improving the adherence, the fish scale resistance and the strength of the enameled steel plate, and the enameled steel plate has the yield strength of more than 310MPa, the tensile strength of more than 410MPa and the elongation of more than 31 percent. The invention does not need to add noble metal elements such as Nb, V, mo and the like, and has good economical efficiency.
Detailed Description
The present invention is described in detail below, but it should be noted that the practice of the present invention is not limited to the following embodiments.
A rare earth hot rolled steel plate for 310 MPa-grade double-sided enamel after enamel, which comprises the following chemical components in percentage by weight: 0.031-0.049% of C, less than or equal to 0.10% of Si, 0.71-0.91% of Mn, 0.065-0.085% of P, 0.012-0.029% of S, 0.66-0.86% of Cr, 0.15-0.18% of Ti, 0.015-0.045% of Als, 0.0061-0.0079% of N, 0.051-0.071% of Sb0.0015-0.0029% of RE, and the balance of Fe and inevitable impurities.
A manufacturing method of a rare earth hot rolled steel plate for 310 MPa-grade double-sided enamel after enamel, which comprises the following process routes: pre-desulfurizing molten steel, performing top and bottom combined blowing of a converter, performing LF external refining, continuously casting a plate blank, heating the plate blank, continuously hot rolling, cooling by laminar flow and coiling; specifically, two-stage rolling control is adopted, a 3+3 mode is adopted for rough rolling, descaling is carried out on each pass of rough rolling, and the outlet temperature of the rough rolling is more than 1100 ℃. The finish rolling adopts 7 stands for continuous rolling, the start temperature of the finish rolling is 1081-1099 ℃, and the finish rolling temperature is 911-935 ℃. After finish rolling, laminar cooling is carried out, the steel is cooled to 619-649 ℃ at the cooling rate of 21-39 ℃/s, and then the steel is air-cooled to room temperature. And front-section centralized cooling is adopted in laminar cooling.
The chemical components of a rare earth hot rolled steel plate for 310 MPa-grade double-sided enamel after enamel are shown in Table 1.
Table 1 shows the chemical compositions in wt% of examples 1 to 10
| Serial number | C | Si | Mn | P | S | Als | Cr | Ti | Sb | RE | N |
| 1 | 0.031 | 0.05 | 0.91 | 0.085 | 0.012 | 0.045 | 0.86 | 0.18 | 0.071 | 0.0029 | 0.0061 |
| 2 | 0.032 | 0.08 | 0.90 | 0.083 | 0.014 | 0.041 | 0.84 | 0.18 | 0.069 | 0.0027 | 0.0063 |
| 3 | 0.033 | 0.03 | 0.89 | 0.081 | 0.016 | 0.038 | 0.82 | 0.18 | 0.067 | 0.0025 | 0.0065 |
| 4 | 0.037 | 0.04 | 0.88 | 0.077 | 0.018 | 0.034 | 0.80 | 0.17 | 0.063 | 0.0024 | 0.0067 |
| 5 | 0.039 | 0.02 | 0.85 | 0.074 | 0.019 | 0.030 | 0.78 | 0.17 | 0.061 | 0.0022 | 0.0069 |
| 6 | 0.041 | 0.09 | 0.83 | 0.073 | 0.021 | 0.027 | 0.76 | 0.16 | 0.058 | 0.0023 | 0.0071 |
| 7 | 0.043 | 0.07 | 0.81 | 0.071 | 0.023 | 0.024 | 0.74 | 0.16 | 0.057 | 0.0021 | 0.0073 |
| 8 | 0.047 | 0.06 | 0.77 | 0.069 | 0.025 | 0.021 | 0.71 | 0.15 | 0.055 | 0.0019 | 0.0075 |
| 9 | 0.048 | 0.04 | 0.74 | 0.067 | 0.027 | 0.018 | 0.68 | 0.15 | 0.053 | 0.0017 | 0.0077 |
| 10 | 0.049 | 0.06 | 0.71 | 0.065 | 0.029 | 0.015 | 0.66 | 0.15 | 0.051 | 0.0015 | 0.0079 |
The rare earth hot rolled steel sheets of examples 1 to 10 having the chemical compositions of Table 1 were manufactured by the following processes:
smelting in a converter, then carrying out external refining, and casting to obtain a continuous casting billet. The thickness of the continuous casting billet is 200-230 mm, the continuous casting billet is sent to a hot rolling production line, the heating outlet temperature of the continuous casting billet is 1252-1281 ℃, the start rolling temperature of finish rolling is 1081-1099 ℃, the finish rolling temperature of the finish rolling is 911-935 ℃, laminar cooling is adopted after rolling, the cooling speed is 21-39 ℃/s, the coiling temperature is 619-649 ℃, and the continuous casting billet is air-cooled to the room temperature after coiling.
The rolling process parameters of the steels of the examples are shown in table 2.
TABLE 2 Rolling Process parameters for examples 1-10
The parameters of the enameling firing process for the steels of the respective examples are shown in table 3.
TABLE 3 enameling firing Process parameters for examples 1-10
| Serial number | Thickness, mm | Enameling temperature of the base glaze lower | Incubation time, min | Enamel firing temperature of the cover glaze DEG C | Incubation time, min |
| Example 1 | 12 | 870 | 18 | 800 | 15 |
| Example 2 | 11 | 870 | 17 | 800 | 14 |
| Example 3 | 10 | 870 | 15 | 800 | 12.5 |
| Example 4 | 9 | 870 | 14 | 800 | 11.5 |
| Example 5 | 8 | 870 | 13 | 800 | 10.5 |
| Example 6 | 7 | 870 | 11 | 800 | 9 |
| Example 7 | 6 | 880 | 10 | 800 | 8 |
| Example 8 | 5 | 880 | 9 | 780 | 8 |
| Example 9 | 4 | 880 | 9 | 780 | 8 |
| Example 10 | 3 | 880 | 9 | 780 | 7.5 |
The mechanical properties of the steels of the examples are shown in Table 4.
TABLE 4 mechanical Properties of examples 1 to 10
The enameling firing temperature of the ground glaze is 870-880 ℃, the enameling firing temperature of the cover glaze is 780-800 ℃, and the enameling firing time of the ground glaze and the cover glaze is correspondingly adjusted according to the different thicknesses of the steel plates. As can be seen from Table 4, the yield strengths before enameling, the tensile strengths and the elongations of the example steels are all more than 510MPa, 620MPa and 21 percent respectively; after enamel is coated, the yield strength is more than 310MPa, the tensile strength is more than 410MPa, and the elongation is more than 31%. And the results of the fish scale explosion resistance performance test are that the fish scale explosion is not generated, the adherence performance is excellent and reaches grade 1, and no pinhole defect exists.
Claims (6)
1. The rare earth hot rolled steel plate for 310 MPa-grade double-sided enamel after enamel is characterized by comprising the following chemical components in percentage by weight:
0.031-0.049% of C, less than or equal to 0.10% of Si, 0.71-0.91% of Mn, 0.065-0.085% of P, 0.012-0.029% of S, 0.66-0.86% of Cr, 0.15-0.18% of Ti, 0.015-0.045% of Als, 0.0061-0.0079% of N, 0.051-0.071% of Sb, 0.0015-0.0029% of RE, and the balance of Fe and inevitable impurities.
2. The rare earth hot-rolled steel sheet for double-sided enameling at the post-enameling level of 310MPa according to claim 1, wherein the steel sheet has a thickness of 3-12 mm, a yield strength of more than 510MPa, a tensile strength of more than 600MPa, and an elongation of more than 21%.
3. The rare earth hot-rolled steel sheet for double-sided enameling at the post-enameling 310MPa level according to claim 1 or 2, wherein the double-sided enameling steel sheet produced by using the steel sheet has yield strength of more than 310MPa, tensile strength of more than 410MPa, and elongation of more than 31%; and the results of the fish scale explosion resistance performance test are that the fish scale explosion is not generated, the adherence performance is excellent and reaches grade 1, and no pinhole defect exists.
4. The rare earth hot-rolled steel sheet for double-sided enameling at a post-enameling level of 310MPa according to claim 3, wherein in the firing process of the double-sided enameled steel sheet: enameling and burning the base glaze at 870-880 ℃ for 9-18min; the enamel firing temperature is 780-800 ℃, and the enamel firing time is 7.5-15min.
5. The method for manufacturing a rare earth hot rolled steel sheet for double-sided enameling at post-enameling 310MPa level according to claim 1 or 2, characterized by comprising the following steps: pre-desulfurizing molten steel, performing top and bottom combined blowing of a converter, performing LF external refining, continuously casting a plate blank, heating the plate blank, continuously hot rolling, cooling by laminar flow and coiling; the method specifically comprises the following steps:
1) The thickness of the casting blank is 200-230 mm; when the slab is heated, controlling the tapping temperature of a casting blank to be 1252-1281 ℃;
2) The hot continuous rolling adopts two-stage controlled rolling, each pass of rough rolling is descaled, and the outlet temperature of the rough rolling is more than 1100 ℃; the initial rolling temperature of finish rolling is 1081-1099 ℃, and the final rolling temperature of finish rolling is 911-935 ℃;
3) After finish rolling, laminar cooling is carried out, the steel is cooled to 619 to 649 ℃ at the cooling rate of 21 to 39 ℃/s, and then the steel is cooled to room temperature by air.
6. The method for producing a rare earth hot-rolled steel sheet for double-sided enameling at post-enameling 310MPa according to claim 5, wherein the laminar cooling employs front-stage concentrated cooling.
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| CN202210767584.XA CN115198184A (en) | 2022-07-01 | 2022-07-01 | Rare earth hot rolled steel plate for 310 MPa-grade double-sided enamel after enamel and manufacturing method thereof |
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| CN202210767584.XA Pending CN115198184A (en) | 2022-07-01 | 2022-07-01 | Rare earth hot rolled steel plate for 310 MPa-grade double-sided enamel after enamel and manufacturing method thereof |
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| CN (1) | CN115198184A (en) |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5651553A (en) * | 1979-10-01 | 1981-05-09 | Nippon Steel Corp | High strength hot rolled steel sheet for both-side enameling |
| JP2006161139A (en) * | 2004-12-10 | 2006-06-22 | Jfe Steel Kk | Hot rolled steel sheet suitable to warm forming and its production method |
| CN1966753A (en) * | 2005-11-16 | 2007-05-23 | 鞍钢股份有限公司 | Steel plate for hot-rolled double-side enamel and method for producing same |
| CN104789899A (en) * | 2015-03-02 | 2015-07-22 | 李宏亮 | Steel hot-rolling plate for double-sided enamels, and preparation process thereof |
| CN106480368A (en) * | 2015-08-31 | 2017-03-08 | 鞍钢股份有限公司 | One kind wards off rear high-strength hot rolled steel plate for counter enameling and its manufacture method |
| CN108624817A (en) * | 2017-03-24 | 2018-10-09 | 宝山钢铁股份有限公司 | One kind warding off rear 310MPa grades of hot-rolled double-side enamel steel and its manufacturing method |
-
2022
- 2022-07-01 CN CN202210767584.XA patent/CN115198184A/en active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5651553A (en) * | 1979-10-01 | 1981-05-09 | Nippon Steel Corp | High strength hot rolled steel sheet for both-side enameling |
| JP2006161139A (en) * | 2004-12-10 | 2006-06-22 | Jfe Steel Kk | Hot rolled steel sheet suitable to warm forming and its production method |
| CN1966753A (en) * | 2005-11-16 | 2007-05-23 | 鞍钢股份有限公司 | Steel plate for hot-rolled double-side enamel and method for producing same |
| CN104789899A (en) * | 2015-03-02 | 2015-07-22 | 李宏亮 | Steel hot-rolling plate for double-sided enamels, and preparation process thereof |
| CN106480368A (en) * | 2015-08-31 | 2017-03-08 | 鞍钢股份有限公司 | One kind wards off rear high-strength hot rolled steel plate for counter enameling and its manufacture method |
| CN108624817A (en) * | 2017-03-24 | 2018-10-09 | 宝山钢铁股份有限公司 | One kind warding off rear 310MPa grades of hot-rolled double-side enamel steel and its manufacturing method |
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