CN109423576B - Hot rolled steel plate for 400 MPa-grade double-sided enamel after enameling and manufacturing method thereof - Google Patents
Hot rolled steel plate for 400 MPa-grade double-sided enamel after enameling 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
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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Abstract
The invention relates to a hot rolled steel plate for 400 MPa-grade double-sided enamel after enamel, which comprises the following chemical components in percentage by mass: c: 0.08 to 0.15 percent; si is less than or equal to 0.10 percent; mn: 1.0% -2.0%; p: 0.060 percent to 0.10 percent; s is less than or equal to 0.006 percent; n is less than or equal to 0.008 percent; ti: 0.02% -0.08%; and Als: 0.010% -0.045%; v: 0.020% -0.055%; nb: 0.01 to 0.05 percent; mo: 0.15 to 0.30 percent, and the balance of Fe and inevitable impurities; when the thickness of the hot rolled steel plate is more than or equal to 8mm, adding B: 0.0005 to 0.005 percent; the yield strength of the hot rolled steel plate after being enameled is more than or equal to 400 MPa. The hot rolled steel plate has good fish scaling resistance, and the yield strength of the hot rolled steel plate after enameling and burning can reach more than 400MPa, so that the requirements of a large-scale enamel assembly structure can be better met.
Description
Technical Field
The invention relates to the technical field of low-alloy hot rolled steel plate production, in particular to a hot rolled steel plate for double-sided enamel and a manufacturing method thereof.
Background
In large-scale water treatment facilities, chemical facilities, environmental protection facilities and biomass energy engineering, the enamel splicing structure is adopted, and the method has the obvious advantages of low investment cost, short construction period, long service life of equipment and the like.
The main material of the enamel assembling structure is a hot rolled steel plate with good double-sided enamel performance. In order to meet the structural design requirements, the thickness of the hot rolled steel plate is generally 3.0 mm-16 mm, and the yield strength level after the steel plate is enameled is generally more than 200 MPa.
Although the cold-rolled enameled steel sheet can meet the requirement of the enamel performance, the thickness specification is mostly below 3mm, the C content is low (below 0.008%), the yield strength after the enamel firing is insufficient, both the specification and the strength can not meet the assembly requirement of large-scale enamel assembling components, and the production cost is high, so the cold-rolled enameled steel sheet is not generally used for enamel assembling structures.
In the hot rolled steel sheet for enamel (e.g., Japanese patent laid-open Nos. 55-152127 and 8-269540), not only the production cost is high due to the high Ti content and the difficulty is high, but also the C content is less than 0.01% and the yield strength after enamel is not sufficiently secured. Japanese patent No. Hei 2-305926 and Japanese patent No. Sho 58-1013 propose a technical proposal of adding B, N, Cu for alloying, but the production process is not easy to control and is not enough to ensure the performance requirements of double-sided enamel.
In the patent documents published in China, the patent technical schemes with the publication numbers of CN200780035777.X, CN200680050708.1, CN03813445.4, CN02821685.7, CN00801729.8 and CN90102120.2 all have the problems that the steel plates are low in C content and low in strength after being enameled, and cannot meet the strength requirement of large-scale assembly structural materials.
The steel sheets proposed in chinese patents CN200810047087.2, CN200610030831.9, and CN200610026267.3 are for single-sided enameling and are not suitable for double-sided enameling.
Chinese patent No. ZL200510047758.1 discloses "a hot-rolled steel sheet for double-sided enamel and a method for manufacturing the same", which discloses a hot-rolled steel sheet for double-sided enamel having a yield strength after firing of 280MPa or more. Under the premise of controlling Ti/C to be more than or equal to 2.2 and less than or equal to 5 in the steel plate, the enamel with a certain amount of foaming agent is matched and added, so that the enamel effect that double-sided enamel is not subjected to scale explosion can be obtained; chinese patent No. 201510548170.8 discloses "a hot rolled steel sheet for high-strength double-sided enameling after enameling and a method for manufacturing the same", wherein the yield strength of the hot rolled steel sheet after enameling is 345MPa or more. However, with the continuous increase of the volume of the enamel assembling structural part, higher requirements are provided for the strength of the steel plate after the enamel is enameled, and the yield strength of the hot rolled steel plate after the enamel is baked in the technical scheme can not meet the requirements of large-scale enamel assembling structural engineering.
Disclosure of Invention
The invention provides a hot rolled steel plate for 400 MPa-grade double-sided enamel after enamel and a manufacturing method thereof, wherein the hot rolled steel plate has good fish scaling resistance, can reach the yield strength of more than 400MPa after enamel firing, and can better meet the requirements of a large-scale enamel assembly structure on steel plate materials.
In order to achieve the purpose, the invention adopts the following technical scheme:
a hot rolled steel plate for 400 MPa-grade double-sided enamel after enamel is prepared from the following chemical components in percentage by mass:
c: 0.08 to 0.15 percent; si is less than or equal to 0.10 percent; mn: 1.0% -2.0%; p: 0.060 percent to 0.10 percent; s is less than or equal to 0.006 percent; n is less than or equal to 0.008 percent; ti: 0.02% -0.08%; and Als: 0.010% -0.045%; v: 0.020% -0.055%; nb: 0.01 to 0.05 percent; mo: 0.15 to 0.30 percent, and the balance of Fe and inevitable impurities;
the thickness of the hot rolled steel plate is 3-16 mm; when the thickness of the hot rolled steel plate is more than or equal to 8mm, adding B into the chemical components, wherein the adding amount is 0.0005-0.005 percent by weight;
the yield strength of the hot rolled steel plate after being enameled is more than or equal to 400 MPa.
A manufacturing method of a hot rolled steel plate for 400 MPa-level double-sided enamel after enameling comprises the production processes of molten steel desulfurization, converter smelting, external refining, continuous casting billet heating, rough rolling, finish rolling, laminar cooling and coiling; wherein:
heating the continuous casting slab to 1180-1250 ℃, carrying out high-pressure water descaling and rough rolling cogging after soaking, carrying out finish rolling at the temperature of 850-1100 ℃, carrying out finish rolling at the temperature of 800-910 ℃, and rapidly cooling to the coiling temperature at the cooling speed of more than or equal to 40 ℃/S after rolling, wherein the coiling temperature is controlled at 560-680 ℃.
Compared with the prior art, the invention has the beneficial effects that:
1) according to the invention, the content of C is controlled to be 0.08-0.15%, the content of Mn is controlled to be 1.0-2.0%, and the P element is added for supplementary reinforcement, so that the yield strength of the hot-rolled steel plate after enamel firing can reach more than 400Pa, and the design requirement of a large-scale assembled structural part can be met;
2) the steel of the invention separates out fine and dispersed TiC, NbC and V (CN) particles by controlling the content of Nb, V and Ti elements in the steel, forms enough hydrogen storage traps and ensures that the hot rolled steel plate has good fish scaling resistance;
3) according to the invention, the B element is selectively added, so that the steel plate still has the yield strength of more than 400MPa after being enameled when the thickness of the steel plate is more than 8 mm;
4) the invention ensures that the steel plate can be stably produced by a continuous casting-continuous rolling method by controlling the Ti content not to exceed 0.08 percent.
Drawings
FIG. 1 is a metallographic structure photograph of a hot-rolled steel sheet in example 1 of the present invention.
Detailed Description
The invention relates to a hot rolled steel plate for 400 MPa-grade double-sided enamel after enamel, which comprises the following chemical components in percentage by mass:
c: 0.08 to 0.15 percent; si is less than or equal to 0.10 percent; mn: 1.0% -2.0%; p: 0.060 percent to 0.10 percent; s is less than or equal to 0.006 percent; n is less than or equal to 0.008 percent; ti: 0.02% -0.08%; and Als: 0.010% -0.045%; v: 0.020% -0.055%; nb: 0.01 to 0.05 percent; mo: 0.15 to 0.30 percent, and the balance of Fe and inevitable impurities;
the thickness of the hot rolled steel plate is 3-16 mm; when the thickness of the hot rolled steel plate is more than or equal to 8mm, adding B into the chemical components, wherein the adding amount is 0.0005-0.005 percent by weight;
the yield strength of the hot rolled steel plate after being enameled is more than or equal to 400 MPa.
A manufacturing method of a hot rolled steel plate for 400 MPa-level double-sided enamel after enameling comprises the production processes of molten steel desulfurization, converter smelting, external refining, continuous casting billet heating, rough rolling, finish rolling, laminar cooling and coiling; wherein:
heating the continuous casting slab to 1180-1250 ℃, carrying out high-pressure water descaling and rough rolling cogging after soaking, carrying out finish rolling at the temperature of 850-1100 ℃, carrying out finish rolling at the temperature of 800-910 ℃, and rapidly cooling to the coiling temperature at the cooling speed of more than or equal to 40 ℃/S after rolling, wherein the coiling temperature is controlled at 560-680 ℃.
Firstly, the selection of the chemical components of the hot rolled steel plate according to the invention is explained as follows:
(1) c is the most economical and effective element for improving the strength, but the welding performance and the cold forming performance of the steel are deteriorated due to the over-high content of C, and the content of C is controlled to be below 0.15 percent, so that the occurrence of the pore defect after enamel can be avoided; therefore, the content of C is controlled between 0.08 percent and 0.15 percent.
(2) The enamel adherence is affected after the Si content exceeds 0.10 percent, so the invention limits the Si to be less than or equal to 0.10 percent.
(3) Mn is a strengthening element, and when the content of C is less than or equal to 0.15 percent, the content of Mn is improved to more than 1.0 percent, so that the yield strength of the steel plate after being enamelfired can reach more than 400 MPa. When the Mn content exceeds 2.0%, the Ac3 temperature of the steel is greatly reduced, and the deformation caused by the austenitizing of the steel plate during the enameling is too large, so the Mn content is controlled within the range of 1.0-2.0%.
(4) P has good solid solution strengthening effect and has no adverse effect on enamel performance. In the invention, when the Mn content is more than 1.0 percent and the P content is more than 0.06 percent, the yield strength of the hot rolled steel plate after enameling firing can reach more than 400 MPa; however, when the content of P exceeds 0.10%, central segregation is easy to occur, which causes the layering of the continuous casting billet and causes adverse effects on the mechanical properties of the steel plate, so the upper limit of the content of P is controlled to be 0.10%, namely the adding range of the P is controlled to be 0.060-0.10%.
(5) When S is more than 0.006%, it causes the Ti precipitated particles to be coarsened, and the total surface area of the Ti precipitated particles as effective hydrogen traps is reduced, so that the content thereof is controlled to not more than 0.006%.
(6) When N is more than 0.008%, excessive precipitation of TiN particles having a diameter of 1 μm or more is likely to occur, which affects the quality of a cast slab and the mechanical properties of the hot-rolled steel sheet, and therefore the upper limit of the content is controlled to 0.008%.
(7) Ti has the functions of grain refinement and precipitation strengthening, and can effectively improve the strength of the steel; ti is also an important forming element of the precipitated particles as a hydrogen trap, and the content thereof is determined to be between 0.02% and 0.08% in order to secure the necessary surface area of the formed hydrogen trap.
(8) Als is a deoxidation product, Al deoxidation is required to be carried out in order to clean the steel, and the cleanliness of the steel can be sufficiently ensured when the Als is 0.010-0.045%; the Als exceeding 0.055% causes an increase in the production cost of steel; therefore, the content of Als is determined to be 0.010-0.045%.
(9) V has good precipitation strengthening effect, and by virtue of the complementary strengthening effect, in the invention, the carbonitride of V can be completely dissolved in gamma-Fe in the enameling process at the temperature of about 900 ℃, so that the main effects of V are interphase precipitation in the gamma → alpha conversion process and precipitation strengthening in ferrite, the strength after enameling can be obviously improved when the content of V reaches 0.020%, but the effect of reaching 0.055% in the invention is saturated, so that the range of V is determined to be 0.020-0.055%.
(10) Nb is an important microalloying element, can improve the temperature of a non-recrystallization area of steel, ensure the effect of rolling control and refine grains after steel rolling; the particles separated by compounding Nb and Ti have precipitation strengthening effect, ensure higher strength of the steel plate after enameling and burning, and are used as hydrogen storage traps, thereby being beneficial to improving the fish scaling resistance of the steel plate; therefore, the content range is determined to be 0.01-0.05%.
(11) Mo has stronger carbide forming capability in steel, and can refine the crystal grains of the steel; mo has a solid solution strengthening effect on ferrite, and simultaneously improves the stability of carbide, thereby improving the strength of the steel; the hot rolled steel plate provided by the invention has a supplementary strengthening effect by virtue of the Mo, and the Mo content is 0.15-0.30%.
(12) The element B is an element selectively added and has the function of inhibiting the strength reduction of the steel plate after the enameling firing. When the thickness specification of the steel plate is not more than 8mm, B does not need to be added, and the yield strength of the steel plate after being enameled can still reach more than 400 MPa; however, when the thickness of the steel sheet exceeds 8mm without adding B, the yield strength in the hot rolled state is lowered due to insufficient cooling rate after rolling, and the yield strength after enameling is insufficient.
The addition of more than 0.0005 percent of B has the function of stabilizing the yield strength of a steel plate with the thickness of more than 8mm to more than 400MPa after being enameled, and the function is saturated when the content of B reaches 0.005 percent; therefore, when B is selectively added, the content of the B is controlled to be 0.0005 to 0.005 percent.
Secondly, the selection of the process parameters in the manufacturing process of the hot rolled steel plate is explained as follows:
(1) the heating temperature of the continuous casting billet is 1180-1250 ℃;
in order to maximize the surface area of a precipitated phase serving as a hydrogen storage trap, Ti precipitated particles in the continuous casting billet are dissolved back into steel as much as possible; at 1180 ℃, most Ti precipitated particles in the continuous casting billet are redissolved, at 1250 ℃, the redissolution degree of the Ti precipitated particles in the steel is close to saturation, and after the heating temperature exceeds 1250 ℃, the damage to heating equipment is increased, the burning loss of the steel is also increased, so that the heating temperature of the casting billet is determined to be 1180-1250 ℃.
(2) The start rolling temperature of finish rolling is 850-1100 ℃, and the finish rolling temperature is 800-910 ℃;
after the finish rolling initial rolling temperature is higher than 1100 ℃, the crystal grains of the finished product are not easy to refine, and the fine grain strengthening effect is not good; when the temperature is lower than 850 ℃, the load of a finish rolling machine frame can be increased, and accidents are easily caused; the finishing temperature is regulated to be more than 850 ℃, so that the condition that the rolling mill is overloaded in a double-phase region by rolling can be avoided, a deformation temperature region which is difficult to control the plate shape is avoided, and the longitudinal and transverse performance difference of the steel plate can be reduced; however, when the finishing temperature is higher than 910 ℃, the grain refinement is insufficient, which affects the strengthening effect.
(3) Rapidly cooling to the coiling temperature at a cooling speed of more than or equal to 40 ℃/S after rolling;
since the range of Ti particle precipitation is wide, the precipitated particles are easily coarsened under slow cooling conditions, the total surface area of precipitated phases is reduced, the total amount of permanent hydrogen storage traps is insufficient, and the strength of the steel sheet is reduced, resulting in insufficient yield strength of the enameled steel sheet. In particular, Ti particles precipitated between phases during the phase transformation are easily coarsened and are disadvantageous in plasticity. Therefore, the present invention adopts a high cooling rate to suppress as much as possible Ti particles having a large periodic distribution generated by interphase deposition. When the cooling rate is not less than 40 ℃/S, it is sufficient to suppress the formation of coarse Ti precipitated particles, and therefore it is determined that the cooling rate after rolling should be not less than 40 ℃/S.
(4) The coiling temperature is controlled to be 560-680 ℃;
in the hot-rolled steel sheet of the invention, when the coiling temperature is lower than 560 ℃, the precipitation of precipitated particles such as TiC as hydrogen storage traps is suppressed, and the total amount of hydrogen storage traps is insufficient to suppress the occurrence of scale explosion. And the coiling temperature is higher than 680 ℃, crystal grains are coarsened, the strength of the hot-rolled steel plate is reduced, and the yield strength after the enameling is insufficient, so the coiling temperature is controlled to be 560-680 ℃.
The following examples are carried out on the premise of the technical scheme of the invention, and detailed embodiments and specific operation processes are given, but the scope of the invention is not limited to the following examples. The methods used in the following examples are conventional methods unless otherwise specified.
[ examples ] A method for producing a compound
In the embodiment, the chemical components of the smelted molten steel are shown in table 1:
TABLE 1
In the embodiment, the production process of the hot rolled steel plate for double-sided enamel comprises the steps of molten steel desulfurization, converter smelting, external refining, continuous casting billet heating, rough rolling, finish rolling, laminar cooling and coiling; wherein:
heating the continuous casting slab to 1180-1250 ℃, carrying out high-pressure water descaling and rough rolling cogging after soaking, carrying out finish rolling at the temperature of 850-1100 ℃, carrying out finish rolling at the temperature of 800-910 ℃, and rapidly cooling to the coiling temperature at the cooling speed of more than or equal to 40 ℃/S after rolling, wherein the coiling temperature is controlled at 560-680 ℃.
The properties of the hot rolled steel sheet produced in this example are shown in Table 2:
TABLE 2
In table 2, the fishscale resistance test means that the steel sheet is left for one month after being double-sided enameled, and the existence of a fishscale point is observed by using a 100-fold microscope.
As can be seen from Table 2, in the example, the 15 batches of hot rolled steel plates produced according to the technical scheme of the invention have the yield strength after the enameling of more than 400MPa, and the results of the fish scaling resistance test are no fish scaling; the yield strength of the hot rolled steel plates produced by the comparison group A and the comparison group B by adopting the conventional method is lower than 400MPa, and the results of the fish scaling resistance test show fish scaling.
As shown in FIG. 1, it is a photograph of a metallographic structure of a hot rolled steel sheet produced in example 1, which had a structure of ferrite + a small amount of pearlite and a grain size of grade 12.
The invention provides a hot rolled steel plate for double-sided enamel with 400MPa grade after enamel and a manufacturing method thereof. As the enameling firing process can coarsen crystal grains, and the fine grain strengthening effect is lost after the enameling firing, the solid solution strengthening and the precipitation hardening are the main strengthening modes for ensuring that the steel plate still keeps high strength after the enameling firing. Through reasonable component design and process control, fine and dispersed TiC, NbC and V (CN) particles are precipitated from the steel, so that sufficient hydrogen storage traps are formed, and the fish scaling resistance of the steel plate is improved; simultaneously, the precipitation strengthening effect of the matrix is separated out, so that the steel plate still keeps higher strength after being enamelfired.
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art should be considered to be within the technical scope of the present invention, and the technical solutions and the inventive concepts thereof according to the present invention should be equivalent or changed within the scope of the present invention.
Claims (1)
1. The manufacturing method of the hot rolled steel plate for 400 MPa-grade double-sided enamel after enamel is characterized in that the hot rolled steel plate comprises the following chemical components in percentage by mass:
c: 0.08 to 0.15 percent; si is less than or equal to 0.10 percent; mn: 1.0% -2.0%; p: 0.060 percent to 0.10 percent; s is less than or equal to 0.006 percent; n is less than or equal to 0.008 percent; ti: 0.02% -0.08%; and Als: 0.010% -0.045%; v: 0.020% -0.055%; nb: 0.01 to 0.025 percent; mo: 0.15 to 0.30 percent, and the balance of Fe and inevitable impurities;
the thickness of the hot rolled steel plate is 3-16 mm; when the thickness of the hot rolled steel plate is more than or equal to 8mm, adding B into the chemical components, wherein the adding amount is 0.0005-0.005 percent by weight;
the after-enameling yield strength of the hot rolled steel plate is more than or equal to 400MPa, the metallographic structure is ferrite and a small amount of pearlite, and the grain size is 12 grades;
the production process of the hot rolled steel plate comprises the steps of molten steel desulfurization, converter smelting, external refining, continuous casting billet heating, rough rolling, finish rolling, laminar cooling and coiling; wherein:
heating the continuous casting slab to 1180-1250 ℃, carrying out high-pressure water descaling and rough rolling cogging after soaking, carrying out finish rolling at the temperature of 850-1100 ℃, carrying out finish rolling at the temperature of 800-910 ℃, and rapidly cooling to the coiling temperature at the cooling speed of more than or equal to 40 ℃/S after rolling, wherein the coiling temperature is controlled at 560-680 ℃.
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| CN101353758A (en) * | 2007-07-23 | 2009-01-28 | 宝山钢铁股份有限公司 | Hot rolling high strength steel plate for two-sided porcelain enamel and manufacturing method thereof |
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