CN112322976A - Rare earth wear-resistant steel NM400 coiled plate with excellent low-temperature-resistant toughness and production method thereof - Google Patents
Rare earth wear-resistant steel NM400 coiled plate with excellent low-temperature-resistant toughness and production 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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- 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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- 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
- C22C38/002—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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- 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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- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- 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
- 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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- 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
- C21D2211/008—Martensite
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Abstract
The invention discloses a rare earth wear-resistant steel NM400 coiled plate with excellent low-temperature-resistant toughness and a production method thereof, wherein the coiled plate comprises the following chemical components in percentage by mass: 0.18-0.20%, Si: 0.30-0.50%, Mn: 1.30-1.45%, P: less than or equal to 0.012%, S: less than or equal to 0.003 percent, Nb: 0.015 to 0.025%, Ti: 0.010-0.025%, Cr: 0.25-0.40%, Ce: 0.0005-0.0015%, Ca: 0.0010-0.0030%, Al: 0.020-0.050%, H: 2ppm or less, O: less than or equal to 30ppm, N: less than or equal to 50ppm, and the balance of Fe and inevitable impurities. The production method is used for producing the thin-specification wear-resistant steel coil plate by rare earth microalloying component design, combining TMCP (thermal mechanical control processing) online quenching technology and adopting a two-stage cooling process, the provided coil plate has excellent low-temperature-resistant toughness and excellent wear resistance, the metallographic structure is ferrite, martensite and a small amount of residual austenite, and the application prospect is wide.
Description
Technical Field
The invention belongs to the technical field of wear-resistant steel, and particularly relates to a rare earth wear-resistant steel NM400 coiled plate with excellent low-temperature-resistant toughness and a production method thereof.
Background
At present, the production of the thin-specification high-strength wear-resistant steel mainly adopts an off-line heat treatment (quenching and tempering) process, the matrix structure of the thin-specification high-strength wear-resistant steel is lath martensite, high strength and hardness are obtained, and the wear resistance is ensured, but the martensite has the characteristic of high brittleness, so that the formability of a steel plate is poorer, the process is long in flow, the requirement on post-rolling heat treatment equipment is high, the cost is high, the production efficiency is low, the yield cannot meet the market demand, and a plurality of obstacles are added for the popularization and application of the thin-specification high-strength wear-resistant steel.
Patent document CN107574370A discloses NM400 wear-resistant steel with the thickness of 2-10 mm and a production method thereof, wherein the steel comprises the following chemical components: 0.10-0.25%, Si: 0.10 to 0.50%, Mn: 0.40-1.40%, P: less than or equal to 0.012 percent, S: less than or equal to 0.005 percent, Cr: 0.20-0.60%, Nb: 0.010-0.060%, Ni: less than or equal to 0.50 percent, Ti: less than or equal to 0.050%, Al: 0.015 to 0.045%, B: 0.0006-0.0025%. The wear-resistant steel produced by the components and the online quenching process disclosed by the document meets the requirements in performance. However, the composition disclosed in the document is alloyed with Ni, so that the alloy cost is high and the provided composition range is wide; the ultra-fast cooling final cooling temperature and the layer cooling start cooling temperature are not provided in the cooling process.
Patent document CN106987760A discloses a method for producing thin-gauge high-Ti wear-resistant steel NM400 by on-line quenching, which comprises the following chemical components: 0.12-0.20%, Si: 0.20-0.40%, Mn: 1.2-1.8%, Mo: 0.15-0.30%, Cr: 0.20-0.50%, Nb: 0.030 to 0.060%, Ti: 0.10-0.15%, Al: 0.015 to 0.045%, B: 0.0006-0.0015%, P: less than or equal to 0.015 percent, S: less than or equal to 0.010 percent, and the steel strip is produced into the wear-resistant steel by adopting the processes of thin slab continuous casting and rolling and ultra-fast cooling quenching. The document adds precious Mo element, Ti element content is high, and alloy cost is high.
Disclosure of Invention
In order to solve one or more problems in the prior art, the invention provides a rare earth wear-resistant steel NM400 coiled plate with excellent low-temperature resistance toughness, which comprises the following chemical components in percentage by mass: 0.18-0.20%, Si: 0.30-0.50%, Mn: 1.30-1.45%, P: less than or equal to 0.012%, S: less than or equal to 0.003 percent, Nb: 0.015 to 0.025%, Ti: 0.010-0.025%, Cr: 0.25-0.40%, Ce: 0.0005-0.0015%, Ca: 0.0010-0.0030%, Als: 0.020-0.050%, H: 2ppm or less, O: less than or equal to 30ppm, N: less than or equal to 50ppm, and the balance of Fe and inevitable impurities.
The chemical components of the rolled plate are as follows by mass percent: 0.18-0.20%, Si: 0.40-0.47%, Mn: 1.36-1.43%, P: less than or equal to 0.012%, S: less than or equal to 0.003 percent, Nb: 0.019 to 0.023 percent, Ti: 0.015-0.022%, Cr: 0.32-0.38%, Ce: 0.0008-0.0010%, Ca: 0.0020 to 0.0022%, Als: 0.033-0.041%, H: 2ppm or less, O: less than or equal to 30ppm, N: less than or equal to 50ppm, and the balance of Fe and inevitable impurities.
The chemical components of the rolled plate comprise the following components in percentage by mass: b: 0.0006-0.0025%.
The mechanical properties of the coiled plate meet the following requirements: the yield strength is more than or equal to 1010MPa, the tensile strength is more than or equal to 1430MPa, the yield ratio is less than or equal to 0.71, the elongation is more than or equal to 13.0 percent, the impact energy at minus 20 ℃ is more than or equal to 72J, the impact energy at minus 40 ℃ is more than or equal to 64J, the impact energy at minus 60 ℃ is more than or equal to 40J, the hardness HV10 is more than or equal to 400, and the metallographic structure is ferrite, martensite and a small amount.
The invention also provides a production method of the rare earth wear-resistant steel NM400 coiled plate, which comprises the following steps: the method comprises the following steps of molten iron pretreatment, converter top and bottom combined blowing smelting, LF external refining, RH vacuum treatment, slab continuous casting, stacking and slow cooling, slab heating, high-pressure water descaling, rough rolling, flying shear, high-pressure water descaling, finish rolling, cooling and coiling; wherein:
the molten iron pretreatment process adopts a KR method to desulfurize molten iron, and ensures that the element S in the molten iron fed into the converter is less than or equal to 0.002%;
the tapping temperature in the converter top-bottom combined blowing smelting process is more than or equal to 1620 ℃;
in the LF external refining process, a large amount of slag is used for slagging and desulfurizing, S is ensured to be less than or equal to 0.003 percent, and ferrochrome and ferrocolumbium are added in the refining process;
in the RH vacuum treatment process, the RH vacuum treatment time is more than 20min, and ferrotitanium and ferroboron are added in the vacuum treatment process; adding rare earth cerium-iron alloy when performing vacuum treatment for 15 min; carrying out calcium treatment on the molten steel after vacuum treatment, wherein the content of Ca is 0.0010-0.0030 percent, and the argon soft blowing time is more than 12 min;
the whole process of the slab continuous casting process is used for protecting pouring, the superheat degree is controlled to be 15-25 ℃, the drawing speed is 0.90-1.10m/min, and a dynamic soft reduction technology is adopted to reduce the center segregation of a continuous casting slab, wherein the center segregation of the casting slab is not more than C3.0 level, and the center porosity is not more than 2.0 level;
the slab heating procedure adopts a stepping heating furnace, the heating temperature is 1190-1230 ℃, and the heating time is more than or equal to 120 min;
in the rough rolling process, an R1 two-roller horizontal reversible rolling mill and an R2 four-roller horizontal reversible rolling mill are adopted for carrying out 3+ 5-pass rolling, and the thickness of an intermediate billet is 40-50 mm;
the finish rolling process adopts a seven-rack four-roller finish rolling unit for rolling, the rolling speed is constant, the finish rolling start temperature is 980-1040 ℃, and the finish rolling temperature is 840-880 ℃;
the cooling process adopts a two-stage cooling mode, the front section adopts encrypted rapid cooling to the temperature of 600-.
The production method of the rare earth wear-resistant steel NM400 coiled plate with excellent low-temperature toughness, which is provided based on the technical scheme, is characterized in that a thin-specification wear-resistant steel coiled plate is produced by low-alloy and trace rare earth component design, a TMCP (thermal mechanical control processing) online quenching technology and a two-stage cooling process, the technical difficulty of obdurability matching under high hardness is overcome, the accurate regulation and control of an online complex phase structure of a thin-specification steel strip is realized, a ferrite soft phase structure is introduced into a harder martensite matrix, the toughness, the plasticity and the formability are increased, the low-temperature toughness of the steel can be effectively improved by combining rare earth, the comprehensive performance advantage of the steel is improved, and the thin-specification wear-resistant steel hot-rolled plate with low cost, low yield ratio, low-temperature toughness, high hardness, high strength and environmental protection is developed. The steel coil is good in plate shape after being uncoiled and straightened, and the steel plate is good in formability and weldability, so that industrial application is realized. The technical problems of long production process flow, high requirement on heat treatment equipment, high strength and hardness, and high low-temperature toughness matching of thin wear-resistant steel are effectively solved.
Drawings
FIG. 1 is a metallographic structure photograph of a rolled sheet obtained in example 1.
Detailed Description
The invention aims to provide a rare earth wear-resistant steel NM400 coiled plate with excellent low-temperature-resistant toughness and a production method thereof.
The production method of the rare earth wear-resistant steel NM400 coiled plate comprises the following processes:
smelting: molten iron pretreatment, converter top and bottom combined blowing smelting, LF external refining, RH vacuum treatment, slab continuous casting and stacking slow cooling;
rolling: heating a plate blank, descaling by high-pressure water, rough rolling by E1R1, rough rolling by E2R2, flying shear, descaling by high-pressure water, and finish rolling by F1-F7;
and (3) cooling: encryption type laminar cooling-coiling-marking-warehousing;
1. smelting
The KR method is adopted to desulfurize molten iron and high-quality scrap steel in the smelting process, and the element S in the molten iron fed into the converter is ensured to be less than or equal to 0.002 percent; when smelting in a converter, self-produced low-sulfur scrap steel is adopted, and the tapping temperature is more than or equal to 1620 ℃. The LF external refining adopts large slag amount for slagging and desulfurizing, ensures that S is less than or equal to 0.003 percent, ferrochromium and ferrocolumbium are added in the refining process, the RH vacuum treatment time is more than 20min, ferrotitanium and ferroboron are added in the early stage of vacuum treatment, rare earth cerium iron alloy (the Ce content is 10-30 percent) is added in 15min of vacuum treatment, the adding amount is less than or equal to 30ppm, and the yield is about 50 percent. RH vacuum treatment ensures the deep vacuum circulation time of the molten steel, calcium treatment is carried out after vacuum treatment, the Ca content of the molten steel after wire feeding is 0.0010-0.0030 percent, and the argon soft blowing time is more than 12min, so that inclusions are fully denatured and float upwards. The whole process is protected and poured during slab continuous casting, the superheat degree is controlled at 15-25 ℃, the drawing speed is 0.90-1.10m/min, and technologies such as dynamic light pressing are adopted to reduce the center segregation of the continuous casting slab, wherein the center segregation of the casting slab is not more than C3.0 level, and the center porosity is not more than 2.0 level.
2. Heating and rolling
The slab heating adopts a stepping heating furnace, the heating temperature is 1190-. The manufacturing process is controlled to be carried out in two stages of hot rolling, all the stages are longitudinal rolling, the first stage is austenite recrystallization zone rolling, namely a rough rolling stage, the rough rolling is carried out for 3+5 times by adopting an R1 two-roller horizontal reversible rolling mill and an R2 four-roller horizontal reversible rolling mill, and the thickness of an intermediate billet is 40-50 mm; the second stage is rolling in an austenite non-recrystallization region, namely a finish rolling stage, wherein the finish rolling is performed by adopting a seven-stand four-roller finish rolling unit, the rolling speed is constant, the finish rolling start temperature is 980-.
3. Cooling down
And after the controlled rolling is finished, the steel strip enters a dense laminar cooling area, the cooling mode is two-stage cooling, the front section is encrypted and rapidly cooled, the cooling temperature is 600-640 ℃, then air cooling is carried out, the air cooling time is 9-12s, the steel strip is rapidly cooled to 100-200 ℃ after air cooling, and coiling is carried out, so that ferrite + martensite and a small amount of residual austenite structures are finally obtained, the grain structures are uniformly distributed, and no mixed crystal and segregation appear.
The present invention is described in detail by the following examples, which are merely illustrative of the embodiments of the present invention and do not limit the content of the present invention.
Example 1
The chemical composition of the rolled sheet is shown in table 1 below. The heating temperature of the plate blank is 1205 ℃, and the heating time is 125 min. Carrying out 3+5 times of rolling on the rough rolling by adopting R1 and R2, wherein the thickness of the intermediate billet is 42 mm; the precision rolling start temperature is 1010 ℃, the finish rolling temperature is 865 ℃, the steel strip enters a laminar flow cooling device after rolling is finished, the cooling mode is two-section cooling, the front section is encrypted and rapidly cooled to 600 ℃, the air cooling time is 10s, the coiling temperature is 120 ℃, and the steel strip can be obtained, wherein the thickness is 6 mm. As shown in FIG. 1, the metallographic structure of the rolled sheet is shown, and the rolled sheet is ferrite + martensite and a small amount of retained austenite, and the grain structure is uniformly distributed without mixed crystals and segregation.
Example 2
The chemical composition of the rolled sheet is shown in table 1 below. The heating temperature of the plate blank is 1220 ℃, and the heating time is 135 min. Carrying out 3+5 times of rolling on the rough rolling by adopting R1 and R2, wherein the thickness of the intermediate billet is 44 mm; the initial rolling temperature of finish rolling is 1020 ℃, the final rolling temperature is 855 ℃, the steel strip enters a laminar cooling device after rolling is finished, the cooling mode is two-section cooling, the front section is encrypted and rapidly cooled to 615 ℃, the air cooling time is 11s, the coiling temperature is 130 ℃, and the steel strip can be obtained, wherein the thickness of the steel strip is 7 mm.
Example 3
The chemical composition of the rolled sheet is shown in table 1 below. The slab heating temperature was 1215 ℃, heating time 130 min. Carrying out 3+5 times of rolling on the rough rolling by adopting R1 and R2, wherein the thickness of the intermediate billet is 46 mm; the start rolling temperature of finish rolling is 1000 ℃, the finish rolling temperature is 860 ℃, the steel strip enters a laminar cooling device after rolling is finished, the cooling mode is two-section type cooling, the front section is encrypted and rapidly cooled to 620 ℃, the air cooling time is 11s, the coiling temperature is 145 ℃, and the steel strip can be obtained, wherein the thickness of the steel strip is 8 mm.
Table 1: examples 1 to 3 chemical Components (wt%)
The mechanical properties of the coils of examples 1 to 3 were tested, and the test results are shown in table 2 below.
Table 2: mechanical properties of the rolled sheets of examples 1 to 3
As can be seen from the data in the table 2, the coil plate produced by the invention has excellent low-temperature-resistant toughness on the basis of ensuring high strength and high wear resistance, wherein the yield strength is more than or equal to 1010MPa, the tensile strength is more than or equal to 1430MPa, the yield ratio is less than or equal to 0.71, the elongation is more than or equal to 13.0 percent, the impact energy at-20 ℃ is more than or equal to 72J, the impact energy at-40 ℃ is more than or equal to 64J, the impact energy at-60 ℃ is more than or equal to 40J, and the hardness HV10 is more. And the plate is good after the plate is rolled and straightened, the flatness of the steel plate can reach 5mm/1m, the formability and the weldability of the steel plate are good, and the industrial application can be realized.
Finally, it should be noted that: although the present invention has been described in detail with reference to the foregoing embodiments, it will be apparent to those skilled in the art that changes may be made in the embodiments and/or equivalents thereof without departing from the spirit and scope of the invention. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (5)
1. The rare earth wear-resistant steel NM400 rolled plate with excellent low-temperature-resistant toughness is characterized by comprising the following chemical components in percentage by mass: 0.18-0.20%, Si: 0.30-0.50%, Mn: 1.30-1.45%, P: less than or equal to 0.012%, S: less than or equal to 0.003 percent, Nb: 0.015 to 0.025%, Ti: 0.010-0.025%, Cr: 0.25-0.40%, Ce: 0.0005-0.0015%, Ca: 0.0010-0.0030%, Als: 0.020-0.050%, H: 2ppm or less, O: less than or equal to 30ppm, N: less than or equal to 50ppm, and the balance of Fe and inevitable impurities.
2. The rare earth wear resistant steel NM400 rolled sheet of claim 1, wherein the rolled sheet has a chemical composition, in mass percent, of C: 0.18-0.20%, Si: 0.40-0.47%, Mn: 1.36-1.43%, P: less than or equal to 0.012%, S: less than or equal to 0.003 percent, Nb: 0.019 to 0.023 percent, Ti: 0.015-0.022%, Cr: 0.32-0.38%, Ce: 0.0008-0.0010%, Ca: 0.0020 to 0.0022%, Als: 0.033-0.041%, H: 2ppm or less, O: less than or equal to 30ppm, N: less than or equal to 50ppm, and the balance of Fe and inevitable impurities.
3. The rare earth wear resistant steel NM400 rolled sheet according to claim 1 or 2, characterized in that the chemical composition of the rolled sheet further comprises, in mass percent: b: 0.0006-0.0025%.
4. The rare earth wear resistant steel NM400 rolled sheet according to claim 1 or 2, wherein the mechanical properties of the rolled sheet satisfy: the yield strength is more than or equal to 1010MPa, the tensile strength is more than or equal to 1430MPa, the yield ratio is less than or equal to 0.71, the elongation is more than or equal to 13.0 percent, the impact energy at minus 20 ℃ is more than or equal to 72J, the impact energy at minus 40 ℃ is more than or equal to 64J, the impact energy at minus 60 ℃ is more than or equal to 40J, the hardness HV10 is more than or equal to 400, and the metallographic structure is ferrite, martensite and a small amount.
5. A method of producing rare earth wear resistant steel NM400 coils as claimed in any of the claims 1-4, comprising the following steps: the method comprises the following steps of molten iron pretreatment, converter top and bottom combined blowing smelting, LF external refining, RH vacuum treatment, slab continuous casting, stacking and slow cooling, slab heating, high-pressure water descaling, rough rolling, flying shear, high-pressure water descaling, finish rolling, cooling and coiling; wherein:
the molten iron pretreatment process adopts a KR method to desulfurize molten iron, and ensures that the element S in the molten iron fed into the converter is less than or equal to 0.002%;
the tapping temperature in the converter top-bottom combined blowing smelting process is more than or equal to 1620 ℃;
in the LF external refining process, a large amount of slag is used for slagging and desulfurizing, S is ensured to be less than or equal to 0.003 percent, and ferrochrome and ferrocolumbium are added in the refining process;
in the RH vacuum treatment process, the RH vacuum treatment time is more than 20min, and ferrotitanium and ferroboron are added in the vacuum treatment process; adding rare earth cerium-iron alloy when performing vacuum treatment for 15 min; carrying out calcium treatment on the molten steel after vacuum treatment, wherein the content of Ca is 0.0010-0.0030 percent, and the argon soft blowing time is more than 12 min;
the whole process of the slab continuous casting process is used for protecting pouring, the superheat degree is controlled to be 15-25 ℃, the drawing speed is 0.90-1.10m/min, and a dynamic soft reduction technology is adopted to reduce the center segregation of a continuous casting slab, wherein the center segregation of the casting slab is not more than C3.0 level, and the center porosity is not more than 2.0 level;
the slab heating procedure adopts a stepping heating furnace, the heating temperature is 1190-1230 ℃, and the heating time is more than or equal to 120 min;
in the rough rolling process, an R1 two-roller horizontal reversible rolling mill and an R2 four-roller horizontal reversible rolling mill are adopted for carrying out 3+ 5-pass rolling, and the thickness of an intermediate billet is 40-50 mm;
the finish rolling process adopts a seven-rack four-roller finish rolling unit for rolling, the rolling speed is constant, the finish rolling start temperature is 980-1040 ℃, and the finish rolling temperature is 840-880 ℃;
the cooling process adopts a two-stage cooling mode, the front section adopts encrypted rapid cooling to the temperature of 600-.
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| CN114855063A (en) * | 2022-04-26 | 2022-08-05 | 湖南华菱湘潭钢铁有限公司 | Production method of corrosion-resistant rare earth steel pipe hot-rolled round steel |
| CN115354232A (en) * | 2022-09-06 | 2022-11-18 | 广西科技大学 | Double-phase wear-resistant steel and preparation method thereof |
| CN115369303A (en) * | 2022-08-08 | 2022-11-22 | 包头钢铁（集团）有限责任公司 | Preparation method of wear-resistant steel NM500 |
| CN115652209A (en) * | 2022-11-07 | 2023-01-31 | 鞍钢股份有限公司 | 650MPa grade sulfuric acid dew point corrosion resistant rare earth steel and manufacturing method thereof |
| CN115896621A (en) * | 2022-11-18 | 2023-04-04 | 江阴兴澄特种钢铁有限公司 | Thin-specification high-quality plate-shaped NM400 steel plate produced by adopting online quenching process and manufacturing method thereof |
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| CN115896621A (en) * | 2022-11-18 | 2023-04-04 | 江阴兴澄特种钢铁有限公司 | Thin-specification high-quality plate-shaped NM400 steel plate produced by adopting online quenching process and manufacturing method thereof |
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