CN113308646B - High-fatigue-performance 700 MPa-grade hot-rolled automobile crossbeam steel strip and preparation method thereof - Google Patents
High-fatigue-performance 700 MPa-grade hot-rolled automobile crossbeam steel strip and preparation method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 51
- 239000010959 steel Substances 0.000 title claims abstract description 51
- 238000002360 preparation method Methods 0.000 title claims abstract description 10
- 238000005096 rolling process Methods 0.000 claims abstract description 52
- 238000001816 cooling Methods 0.000 claims abstract description 37
- 239000000126 substance Substances 0.000 claims abstract description 11
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 9
- 238000010438 heat treatment Methods 0.000 claims abstract description 8
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 5
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 238000005266 casting Methods 0.000 claims description 14
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 5
- 241000007534 Acacia tetragonophylla Species 0.000 claims description 3
- 229910045601 alloy Inorganic materials 0.000 claims description 3
- 239000000956 alloy Substances 0.000 claims description 3
- 238000000034 method Methods 0.000 abstract description 11
- 238000009749 continuous casting Methods 0.000 abstract description 4
- 238000003723 Smelting Methods 0.000 abstract description 3
- 238000009628 steelmaking Methods 0.000 abstract description 2
- 238000005098 hot rolling Methods 0.000 abstract 1
- 239000010936 titanium Substances 0.000 description 13
- 230000000052 comparative effect Effects 0.000 description 9
- 230000008569 process Effects 0.000 description 7
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 2
- 238000004886 process control Methods 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- RMLPZKRPSQVRAB-UHFFFAOYSA-N tris(3-methylphenyl) phosphate Chemical compound CC1=CC=CC(OP(=O)(OC=2C=C(C)C=CC=2)OC=2C=C(C)C=CC=2)=C1 RMLPZKRPSQVRAB-UHFFFAOYSA-N 0.000 description 1
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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
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- 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
-
- 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
-
- 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
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
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Abstract
The invention discloses a high-fatigue-performance 700 MPa-grade hot-rolled automobile beam steel strip and a preparation method thereof, belonging to the technical field of steel making. The high fatigue performance 700MPa level hot rolling automobile beam steel belt comprises the following chemical components in percentage by mass: 0.02 to 0.06 percent of C, less than or equal to 0.08 percent of Si, 1.0 to 2.0 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.01 percent of S, 0.08 to 0.35 percent of Ti, less than or equal to 0.005 percent of N, the balance of Fe and inevitable impurities, the microstructure comprises 90 to 98 percent of ferrite and 2 to 10 percent of acicular bainite, and the grain size grade is 12 to 13 grades. The preparation method sequentially comprises the steps of smelting, continuous casting, heating, rough rolling, UFC intermediate billet cooling, finish rolling, laminar cooling and coiling. The 700 MPa-grade hot-rolled automobile crossbeam steel strip produced by the method has excellent surface quality, fatigue performance, forming performance and toughness performance, and can effectively solve the problem of poor fatigue performance of the conventional 700 MPa-grade hot-rolled automobile crossbeam steel strip.
Description
Technical Field
The invention belongs to the technical field of steel making, relates to a hot-rolled automobile beam steel plate, and particularly relates to a 700 MPa-level hot-rolled automobile beam steel strip with high fatigue performance and a preparation method thereof.
Background
In recent years, due to the double pressure of reduction and national six standards (GB 17691-. However, the research on the fatigue limit regulation and mechanism of the 700MPa automobile frame steel plate is rarely reported. The adoption of high-strength steel is an effective way for the reduction and sustainable development of automobiles, and the problems of low material fatigue performance and fracture seriously restrict the sustainable development of the heavily loaded automobile industry because the high-strength steel not only bears the nonlinear bending load vertical to the plane of the chassis but also bears the longitudinal instantaneous impact load under the service condition. Therefore, the research on the fatigue property of the hot rolled steel has important significance, and the development of the hot rolled automobile frame steel strip with high fatigue property is necessary.
Disclosure of Invention
The invention aims to solve the technical problem that the existing 700 MPa-grade hot-rolled automobile girder steel strip has poor fatigue performance.
The technical scheme adopted by the invention for solving the technical problems is as follows: the high-fatigue-performance 700 MPa-grade hot-rolled automobile beam steel strip comprises the following chemical components in percentage by mass: 0.02 to 0.06 percent of C, less than or equal to 0.08 percent of Si, 1.0 to 2.0 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.01 percent of S, 0.08 to 0.35 percent of Ti, less than or equal to 0.005 percent of N, the balance of Fe and inevitable impurities, the microstructure of the alloy is 90 to 98 percent of ferrite and 2 to 10 percent of acicular bainite, and the grain size grade is 12 to 13.
The preparation method of the 700 MPa-level high-fatigue-performance hot-rolled automobile girder steel strip sequentially comprises the steps of smelting, continuous casting, heating, rough rolling, UFC intermediate billet cooling, finish rolling, laminar cooling and coiling, and specifically comprises the following steps:
a. preparing a casting blank according to chemical components of a 700 MPa-grade hot-rolled automobile girder steel strip with high fatigue performance;
b. rough rolling: rolling the heated casting blank into a plate blank, carrying out 3+3 mode rough rolling on the thin plate blank, and controlling the first-pass deformation to be more than or equal to 20%, the last-pass deformation to be more than or equal to 35% and the accumulated deformation to be more than or equal to 80%; roughly rolling a thick plate blank in a 0+5 mode, controlling the first-pass deformation to be more than or equal to 20 percent, the last-pass deformation to be more than or equal to 35 percent, controlling the accumulated deformation of the rear 2 machine frame to be more than or equal to 50 percent, and controlling the accumulated deformation to be more than or equal to 78 percent;
and c, cooling the UFC intermediate blank: rapidly cooling the rough-rolled plate blank to 930 +/-20 ℃ at the speed of 80-150 ℃/s;
d. finish rolling: and (3) carrying out continuous rolling for 5-7 times, controlling the deformation of the last frame to be 8-15%, and controlling the accumulated deformation of the last 3 frames to be 20-35%.
In the step b, the thickness of the plate blank is 40-50mm, the thickness of the thin plate blank is 40-44mmm, and the thickness of the thick plate blank is 45-50 mm.
In the step b, the heating temperature of the casting blank is 1260 +/-20 ℃, and the temperature is kept for 100-180 min.
The finishing temperature of the finish rolling is 830-890 ℃.
And after finishing the finish rolling, adopting two-stage cooling, rapidly cooling to 600-700 ℃ at the speed of 60-100 ℃/s, then air cooling for 3-8s, and then continuously cooling at the speed of 0-100 ℃/s.
The final coiling temperature was 480-580 ℃.
In the steps b and d, after rolling is finished, high-pressure water is adopted for dephosphorization, and the water pressure is 20 MPa.
The invention has the beneficial effects that: according to the invention, the strength of steel is improved by quantitatively designing the Ti content, the microstructure of the produced crossbeam steel strip is 90-98% of ferrite and 2-10% of acicular bainite by combining the control of the full-process, particularly the control of the UFC intermediate billet cooling process and the rolling deformation, the grain size grade is 12-13 grade, and the stable control of the 700MPa grade hot-rolled automobile crossbeam steel strip with high fatigue performance is realized. The 700 MPa-grade hot-rolled automobile crossbeam steel strip produced by the method has excellent surface quality, fatigue performance, forming performance and toughness performance.
Ti can improve the strength of steel through supersaturated precipitation in ferrite, and the formula is that Ti (effective titanium) ═ Ti (total) -3.4N-3S exists in the steel, and S is combined with Ti to easily form Ti4C2S2N and Ti are combined to form liquated TiN easily in the continuous casting process, however, S, N and other elements in steel cannot be avoided, and therefore a reasonable TMCP process needs to be matched. The invention controls the heating of the casting blank to inhibit Ti 4C2S2And coarsening and growing up the liquated TiN; simultaneously controlling the deformation in the rolling process to control the deformation induction phase change in austenite, and simultaneously enabling the Ti with large size in the early stage4C2S2And liquating TiN to break and homogenize; the growth of a steel strip structure after a rough rolling process is inhibited through the cooling of the UFC intermediate blank, the uniformity of a matrix structure and the size and the quantity of precipitated phases in ferrite are controlled, particularly the coarsening of the precipitated phases which are not dissolved back at the early stage is controlled, and the steel strip structure can be controlled to be relatively large in cooperation with other proceduresThe small range contributes to improvement of fatigue property of the steel sheet.
Detailed Description
The technical solution of the present invention can be specifically implemented as follows.
The high fatigue performance 700MPa level hot rolled automobile beam steel strip comprises the following chemical components in percentage by mass: 0.02 to 0.06 percent of C, less than or equal to 0.08 percent of Si, 1.0 to 2.0 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.01 percent of S, 0.08 to 0.35 percent of Ti, less than or equal to 0.005 percent of N, the balance of Fe and inevitable impurities, the microstructure of the alloy is 90 to 98 percent of ferrite and 2 to 10 percent of acicular bainite, and the grain size grade is 12 to 13.
The preparation method of the 700 MPa-grade high-fatigue-performance hot-rolled automobile beam steel strip sequentially comprises the steps of smelting, continuous casting, heating, rough rolling, UFC intermediate billet cooling, finish rolling, laminar cooling and coiling, and specifically comprises the following steps:
a. Preparing a casting blank according to chemical components of a 700 MPa-grade hot-rolled automobile girder steel strip with high fatigue performance;
b. rough rolling: rolling the heated casting blank into a plate blank, carrying out 3+3 mode rough rolling on the thin plate blank, and controlling the first-pass deformation to be more than or equal to 20%, the last-pass deformation to be more than or equal to 35% and the accumulated deformation to be more than or equal to 80%; roughly rolling a thick plate blank in a 0+5 mode, controlling the first-pass deformation to be more than or equal to 20 percent, the last-pass deformation to be more than or equal to 35 percent, controlling the accumulated deformation of the rear 2 machine frame to be more than or equal to 50 percent, and controlling the accumulated deformation to be more than or equal to 78 percent;
and c, cooling the UFC intermediate blank: rapidly cooling the rough-rolled plate blank to 930 +/-20 ℃ at the speed of 80-150 ℃/s;
d. finish rolling: and (3) carrying out continuous rolling for 5-7 times, controlling the deformation of the last frame to be 8-15%, and controlling the accumulated deformation of the last 3 frames to be 20-35%.
After the casting blank is taken out of the heating furnace, the thickness of the casting blank is 200-230mm, and the casting blank is rolled to a plate blank by 2 roughing mill groups, wherein the thickness of the plate blank is 40-50 mm. In order to produce hot rolled plates of 2mm to 14mm, it is therefore preferable to use 3+3 mode for the rough rolling process of thin gauge slabs with a thickness of 40 to 44mmm, i.e. six passes of rough rolling, ensuring the amount of deformation per pass; the 0+5 mode is adopted in the rough rolling process of the thick plate blank with the thickness of 45-50mm, namely 5 passes of rolling are carried out, and one rolling mill has no reduction.
In order to control the re-dissolution of the fine TiC and simultaneously inhibit the coarsening growth of Ti4C2S2 and liquated TiN, it is preferable that the heating temperature of the casting blank in the step b is 1260 +/-20 ℃, and the temperature is kept for 100-180 min.
In order to control the TiC deformation induced precipitation amount, the TiC deformation induced precipitation amount is preferably subjected to 5-7 passes of continuous rolling by 7 finishing mill sets, the F7 deformation amount is 8-15%, the accumulated deformation amount of the rear 3 stands is 20-35%, and the finishing rolling temperature is 830-890 ℃.
In order to control the uniformity of the matrix structure, it is preferable to adopt two-stage cooling, after the end rolling, adopting rapid cooling to the ferrite region, and rapidly cooling to 600-; then air cooling is carried out, the transformation amount and precipitation of ferrite are controlled, and the air cooling time is 3-8 s; cooling to bainite at 0-100 deg.c/s speed and final plate band coiling temperature of 480-580 deg.c.
In order to better control the chemical composition of the steel, it is preferable that in the steps b and d, after the rolling is completed, high-pressure water is used for removing phosphorus, and the water pressure is 20 MPa.
The technical solution and effects of the present invention will be further described below by way of practical examples.
Examples
This example provides 1 group of 700MPa grade hot-rolled automotive frame steel strips with high fatigue properties prepared by the preparation method of the present invention and two groups of comparative examples, and the chemical compositions of the automotive frame steel strip slabs are shown in table 1.
Chemical composition (wt.%) of hot-rolled girder steel slab with table 1700 MPa grade
| Number of | C | Si | Mn | P | S | N | Ti |
| Example 1 | 0.036 | 0.047 | 1.56 | 0.008 | 0.002 | 0.002 | 0.25 |
| Comparative example 1 | 0.052 | 0.074 | 1.92 | 0.012 | 0.008 | 0.0046 | 0.33 |
| Comparative example 2 | 0.080 | 0.083 | 0.89 | 0.012 | 0.010 | 0.0055 | 0.07 |
And (3) rolling the heated casting blank into a slab, and then roughly rolling the slab, wherein the main process control parameters of the rough rolling of the slab are shown in a table 2.
Table 2700 MPa hot-rolled girder steel strip rough rolling process
Cooling an UFC intermediate blank: the slab after rough rolling was rapidly cooled and the control parameters are shown in table 3.
Table 3700 MPa-level hot-rolled girder steel strip UFC rapid cooling process
| Numbering | Thickness of slab/mm | Cooling Rate/. degree.C/s | Cooling temperature/. degree.C |
| Example 1 | 41 | 90 | 930 |
| Comparative example 1 | 50 | 79 | 960 |
| Comparative example 2 | 43 | 90 | 928 |
After 5-7 passes of continuous rolling by 7 finishing mill groups, the control parameters of the finishing rolling procedure are shown in table 4.
Finish rolling process for hot-rolled crossbeam steel strip in Table 4700 MPa level
After finishing the finish rolling, the process of layer cooling is carried out, and then coiling is carried out, wherein the main process control parameters are shown in the table 5.
Surface 5700 MPa-level hot-rolled girder steel strip layer cooling process
| Numbering | Cooling rate at 1 stage/° C/s | Air cooling time/s | 2-stage cooling rate/° C/s | Coiling temperature/. degree.C |
| Example 1 | 78 | 5 | 40 | 550 |
| Comparative example 1 | 58 | 3 | 56 | 580 |
| Comparative example 2 | 83 | 5 | 67 | 520 |
The automobile frame steel strip prepared by the process is subjected to mechanical test, and the mechanical properties of the automobile frame steel strip are shown in table 6.
Mechanical properties of hot-rolled girder steel strip of surface 6700 MPa level
The embodiment and the comparative example show that the high fatigue property 700 MPa-grade hot-rolled automobile girder steel strip prepared by the chemical components and the preparation method has obviously better fatigue property than the comparative example, excellent surface quality, excellent forming property and excellent toughness property.
Claims (7)
1. The high-fatigue-performance 700 MPa-grade hot-rolled automobile beam steel strip is characterized by comprising the following chemical components in percentage by mass: 0.02 to 0.06 percent of C, less than or equal to 0.08 percent of Si, 1.0 to 2.0 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.01 percent of S, 0.08 to 0.35 percent of Ti, less than or equal to 0.005 percent of N, the balance of Fe and inevitable impurities, the microstructure of the alloy is 90 to 98 percent of ferrite and 2 to 10 percent of acicular bainite, and the grain size grade is 12 to 13;
the preparation method of the 700 MPa-grade hot-rolled automobile beam steel strip with high fatigue performance comprises the following steps:
a. preparing a casting blank according to the chemical components of the 700 MPa-grade hot-rolled automobile girder steel strip with high fatigue performance;
b. rough rolling: rolling the heated casting blank into a plate blank, carrying out 3+3 mode rough rolling on the thin plate blank, and controlling the first-pass deformation to be more than or equal to 20%, the last-pass deformation to be more than or equal to 35% and the accumulated deformation to be more than or equal to 80%; roughly rolling a thick plate blank in a 0+5 mode, controlling the first-pass deformation to be more than or equal to 20 percent, the last-pass deformation to be more than or equal to 35 percent, controlling the accumulated deformation of the rear 2 machine frame to be more than or equal to 50 percent, and controlling the accumulated deformation to be more than or equal to 78 percent;
and c, cooling the UFC intermediate blank: rapidly cooling the rough-rolled plate blank to 930 +/-20 ℃ at the speed of 80-150 ℃/s;
d. finish rolling: and (5) carrying out 5-7-pass continuous rolling, and controlling the deformation of the last rack to be 8-15% and the accumulated deformation of the last 3 racks to be 20-35%.
2. The high fatigue property 700MPa grade hot rolled automobile frame steel strip according to claim 1, characterized in that: in the step b, the thickness of the plate blank is 40-50mm, the thickness of the thin plate blank is 40-44mm, and the thickness of the thick plate blank is 45-50 mm.
3. The high fatigue performance 700MPa grade hot rolled automotive frame steel strip of claim 1, wherein: in the step b, the heating temperature of the casting blank is 1260 +/-20 ℃, and the temperature is kept for 100-180 min.
4. The high fatigue performance 700MPa grade hot rolled automotive frame steel strip of claim 1, wherein: the finish rolling temperature of the finish rolling is 830-890 ℃.
5. The high fatigue performance 700MPa grade hot rolled automotive frame steel strip of claim 1, wherein: after finishing the finish rolling, adopting two-stage cooling, rapidly cooling to 600-700 ℃ at the speed of 60-100 ℃/s, then air cooling for 3-8s, and continuing cooling at the speed of 0-100 ℃/s.
6. The high fatigue performance 700MPa grade hot rolled automotive frame steel strip of claim 1, wherein: the final coiling temperature is 480-580 ℃.
7. The high fatigue performance 700MPa grade hot rolled automotive frame steel strip of claim 1, wherein: in the steps b and d, high-pressure water is adopted for dephosphorization after the rolling is finished.
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