CN104451407B - A kind of low-carbon hot-rolling ultra-high-strength/tenacity steel and preparation method thereof - Google Patents
A kind of low-carbon hot-rolling ultra-high-strength/tenacity steel and preparation method thereof Download PDFInfo
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Abstract
A kind of low-carbon hot-rolling ultra-high-strength/tenacity steel and preparation method thereof, belongs to metallurgical technology field, and the composition of high-strength and high-toughness steel is by weight percentage containing C 0.10 ~ 0.11%, Si 1.35 ~ 1.5%, Mn 1.85 ~ 2.0%, Cr 0.7 ~ 0.8%, Mo 0.28 ~ 0.3%, P≤0.004%, S≤0.003%, surplus is Fe；Yield strength is 900 ~ 980MPa, and it is 86.8 ~ 117.8J that 20 DEG C of low-temperature impacts absorb merit；Preparation method sequentially includes the following steps: (1) and makes strand by set component smelting, refine and cast, strand is reheated to austenitizing temperature, is incubated more than 2.5 hours, is forged into steel billet at 950 ~ 1050 DEG C；(2) it is heated to 1200 ± 10 DEG C and is incubated at least 2 hours, carry out first stage rolling in austenite recrystallization district and austenite Unhydrated cement respectively and second stage rolls, it is thus achieved that hot rolled steel plate；(3) being cooled to 180 ± 20 DEG C with the cooling rate of 60 ~ 90 DEG C/s, then air cooling is to room temperature.It is reasonable in design that the present invention has composition, the feature that technology controlling and process is simple and easy to do, and uses online direct quenching, and without tempering process, therefore production efficiency is high, energy consumption is low, it is thus achieved that steel there is the intensity of superelevation and good low-temperature flexibility.
Description
Technical field
The invention belongs to metallurgical technology field, particularly to a kind of low-carbon hot-rolling ultra-high-strength/tenacity steel and preparation method thereof.
Background technology
In recent years, along with increasing sharply of high-strength structure part and engineering machinery, going from bad to worse of Service Environment, structural steel develops towards higher intensity and good low-temperature flexibility direction.In order to reduce production cost, improve combination property, especially solve the contradiction that intensity improves and welding performance declines, under ensureing excellent low-temperature flexibility and welding performance premise, by suitable Reasonable adjustment alloying element content and further improvement controlled rolling and Controlled cooling process, elongation percentage and fracture toughness can be made all to have the biggest lifting.
The Chinese patent application of Application No. 200510024756 discloses " a kind of superhigh strength steel plate with yield strength more than 1100 Mpa and manufacture method ", this invention optimizes tradition and reheats the modulation process of quenching+tempering, but employing press quenching, shortened process improves production efficiency, but the method must carry out tempering process, its yield strength of five embodiments after tempering process is all higher than 1100MPa, and elongation percentage is more than or equal to 13%, the ballistic work 36 ~ 47J of-20 DEG C；The Chinese patent application of Application No. 201110096170.0 and the Chinese patent application of Application No. 201410089398.0 all propose the preparation technology of quenching+lonneal, obtain the above super-high strength steel of yield strength 1100MPa, elongation percentage is all between 11 ~ 15%, and-20 C ballistic works are about 45J；From contrasting patent above, although this type of patent obtains the highest intensity, but inevitably all have employed tempering process, do not significantly increase production efficiency.
The Chinese patent application of Application No. 200610051936 discloses " 1100MPa level Micro Alloying high-strength steel and production method thereof ", this invention needs to carry out the cold rolling process of 70-80% heavy reduction on the basis of hot rolling, the 1100MPa level Micro Alloying high-strength steel that elongation percentage is 10.5 ~ 12.5% could be obtained, its technique is the most complicated, and cost is the highest.
Summary of the invention
For existing 1100MPa level above ultra-high-strength/tenacity steel in the problems referred to above present on preparation method and performance, the present invention provides a kind of low-carbon hot-rolling ultra-high-strength/tenacity steel and preparation method thereof, designed by rational composition, avoid the fragility that quenches, use online direct quenching and need not any tempering process, making the ultra-high-strength/tenacity steel of intensity and low-temperature good toughness.
The composition of the low-carbon hot-rolling ultra-high-strength/tenacity steel of the present invention is by weight percentage containing C 0.10 ~ 0.11%, Si 1.35 ~ 1.5%, Mn
1.85 ~ 2.0%, Cr 0.7 ~ 0.8%, Mo 0.28 ~ 0.3%, P≤0.004%, S≤0.003%, surplus is Fe；Yield strength is 900 ~ 980MPa, and it is 86.8 ~ 117.8J that-20 DEG C of low-temperature impacts absorb merit.
The tensile strength of above-mentioned low-carbon hot-rolling ultra-high-strength/tenacity steel is 1140 ~ 1300MPa, and elongation percentage is 13.8 ~ 18.8%.
The heterogeneous structure being organized as bainite, martensite and retained austenite of above-mentioned low-carbon hot-rolling ultra-high-strength/tenacity steel.
The preparation method of the low-carbon hot-rolling ultra-high-strength/tenacity steel of the present invention sequentially includes the following steps:
1, making strand by set component smelting, refine and cast, strand is reheated to austenitizing temperature, heating and temperature control, at 1050 ~ 1100 DEG C, is incubated more than 2.5 hours, is then forged into steel billet in 950 ~ 1050 DEG C of temperature ranges；
2, heating steel billet to 1200 ± 10 DEG C is incubated at least 2 hours, carry out first stage rolling in austenite recrystallization district and austenite Unhydrated cement respectively and second stage rolls, the start rolling temperature scope of first stage is 1130 ~ 1150 DEG C, and finishing temperature control is more than 1100 DEG C；The start rolling temperature scope of second stage is 930 ~ 950 DEG C, and finishing temperature control is between 900 ~ 930 DEG C；The total reduction of first paragraph rolling is 35 ~ 40%, and the total reduction of second stage is 75 ~ 80%, it is thus achieved that hot rolled steel plate；
3, with the cooling rate of 60 ~ 90 DEG C/s, hot rolled steel plate being cooled to 180 ± 20 DEG C, then air cooling is to room temperature, it is thus achieved that low-carbon hot-rolling ultra-high-strength/tenacity steel.
The composition mentality of designing of the present invention is:
1, in order to improve the welding performance of ultra-high-strength/tenacity steel, reducing the cool attenuation of welded steel, reduce carbon equivalent, and carbon is to determine the topmost element of carbon equivalent, therefore uses the composition of low-carbon (LC) to design, C content controls between 0.10 ~ 0.11%；
2, in order to obtain superhigh intensity, main Cr, Mn element using relative low price improves hardenability of steel, and Cr content controls between 0.7 ~ 0.8%, and Mn content controls between 1.85 ~ 2.0%；Adding appropriate Mo element to improve steel strength further, Mo content controls between 0.28 ~ 0.3% simultaneously.
3, in order under Micro Alloying state after quenching, good low-temperature impact toughness is ensure that while obtaining superhigh intensity, the phase of infringement steel toughness must be reduced, therefore higher Si content is used, improve the activity of carbon, it is unfavorable for the formation of cementite, reduces the formation of crack in impact process, significantly improve low-temperature impact toughness.
4, p and s element seriously damages plasticity and the toughness of steel, it is therefore desirable to steel is carried out Refining, the strict content controlling p and s, it is ensured that the plasticity of steel and toughness.
It is reasonable in design that the present invention has composition, the feature that technology controlling and process is simple and easy to do, and uses online direct quenching, and without tempering process, therefore production efficiency is high, energy consumption is low, it is thus achieved that steel there is the intensity of superelevation and good low-temperature flexibility.
Accompanying drawing explanation
Fig. 1 is the metallographic structure microgram of the hot rolled steel plate of the embodiment of the present invention 1；
Fig. 2 is the metallographic structure microgram of the hot rolled steel plate of the embodiment of the present invention 2.
Detailed description of the invention
The direct quenching cooling device used in the embodiment of the present invention is Northeastern University's rolling technique and tandem rolling automatization independent development ultra-rapid cooling experiment quenching press.
The embodiment of the present invention is observed the equipment of metallographic structure for coming card DMIRM 2500M metallurgical microscope.
The embodiment of the present invention is forged in 950 ~ 1050 DEG C of temperature ranges steel billet refer to forge by forging ratio 1.5 ~ 1.7.
Embodiment 1
Making strand by set component smelting, refine and cast, strand composition is by weight percentage containing C 0.10%, Si 1.43%, Mn 1.85%, Cr 0.7%, Mo 0.28%, P 0.003%, S 0.003%, and surplus is Fe；
Strand is reheated to austenitizing temperature, and heating and temperature control, at 1050 DEG C, is incubated 2.5 hours, is then forged into steel billet (forging by forging ratio 1.7) in 950 ~ 1050 DEG C of temperature ranges；
Heating steel billet to 1200 ± 10 DEG C being incubated 2 hours, carries out first stage rolling in austenite recrystallization district and austenite Unhydrated cement respectively and second stage rolls, the start rolling temperature of first stage is 1130 DEG C, and finishing temperature control is at 1100 DEG C；The start rolling temperature of second stage is 930 DEG C, and finishing temperature control is at 900 DEG C；The total reduction of first paragraph rolling is 40%, and the total reduction of second stage is 75%, it is thus achieved that hot rolled steel plate；
With the cooling rate of 80 ~ 90 DEG C/s, hot rolled steel plate is cooled to 180 ± 20 DEG C, and then air cooling is to room temperature, it is thus achieved that low-carbon hot-rolling ultra-high-strength/tenacity steel, and yield strength is 980MPa, and it is 86.8J that-20 DEG C of low-temperature impacts absorb merit；Tensile strength is 1300MPa, and elongation percentage is 13.8%；It is organized as the heterogeneous structure of bainite, martensite and retained austenite.
Embodiment 2
Making strand by set component smelting, refine and cast, strand composition is by weight percentage containing C 0.11%, Si 1.35%, Mn 1.89%, Cr 0.8%, Mo 0.29%, P 0.004%, S 0.002%, and surplus is Fe；
Strand is reheated to austenitizing temperature, and heating and temperature control, at 1080 DEG C, is incubated 3 hours, is then forged into steel billet (forging by forging ratio 1.5) in 950 ~ 1050 DEG C of temperature ranges；
Heating steel billet to 1200 ± 10 DEG C being incubated 3 hours, carries out first stage rolling in austenite recrystallization district and austenite Unhydrated cement respectively and second stage rolls, the start rolling temperature of first stage is 1140 DEG C, and finishing temperature control is at 1110 DEG C；The start rolling temperature of second stage is 940 DEG C, and finishing temperature control is at 920 DEG C；The total reduction of first paragraph rolling is 35%, and the total reduction of second stage is 78%, it is thus achieved that hot rolled steel plate；
With the cooling rate of 70 ~ 80 DEG C/s, hot rolled steel plate is cooled to 180 ± 20 DEG C, and then air cooling is to room temperature, it is thus achieved that low-carbon hot-rolling ultra-high-strength/tenacity steel, and yield strength is 940MPa, and it is 102.6J that-20 DEG C of low-temperature impacts absorb merit；Tensile strength is 1220MPa, and elongation percentage is 15.9%；It is organized as the heterogeneous structure of bainite, martensite and retained austenite.
Embodiment 3
Making strand by set component smelting, refine and cast, strand composition is by weight percentage containing C 0.10%, Si 1.4%, Mn 1.92%, Cr 0.7%, Mo 0.3%, P 0.001%, S 0.002%, and surplus is Fe；
Strand is reheated to austenitizing temperature, and heating and temperature control, at 1100 DEG C, is incubated 2.5 hours, is then forged into steel billet (forging by forging ratio 1.7) in 950 ~ 1050 DEG C of temperature ranges；
Heating steel billet to 1200 ± 10 DEG C being incubated 2.5 hours, carries out first stage rolling in austenite recrystallization district and austenite Unhydrated cement respectively and second stage rolls, the start rolling temperature of first stage is 1150 DEG C, and finishing temperature control is at 1120 DEG C；The start rolling temperature of second stage is 950 DEG C, and finishing temperature control is at 930 DEG C；The total reduction of first paragraph rolling is 40%, and the total reduction of second stage is 80%, it is thus achieved that hot rolled steel plate；
With the cooling rate of 60 ~ 70 DEG C/s, hot rolled steel plate is cooled to 180 ± 20 DEG C, and then air cooling is to room temperature, it is thus achieved that low-carbon hot-rolling ultra-high-strength/tenacity steel, and yield strength is 900MPa, and it is 117.8J that-20 DEG C of low-temperature impacts absorb merit；Tensile strength is 1140MPa, and elongation percentage is 18.8%；It is organized as the heterogeneous structure of bainite, martensite and retained austenite.
Embodiment 4
Making strand by set component smelting, refine and cast, strand composition is by weight percentage containing C 0.11%, Si 1.45%, Mn 1.96%, Cr 0.8%, Mo 0.28%, P 0.003%, S 0.001%, and surplus is Fe；
Strand is reheated to austenitizing temperature, and heating and temperature control, at 1050 DEG C, is incubated 3 hours, is then forged into steel billet (forging by forging ratio 1.6) in 950 ~ 1050 DEG C of temperature ranges；
Heating steel billet to 1200 ± 10 DEG C being incubated 2 hours, carries out first stage rolling in austenite recrystallization district and austenite Unhydrated cement respectively and second stage rolls, the start rolling temperature of first stage is 1130 DEG C, and finishing temperature control is at 1100 DEG C；The start rolling temperature of second stage is 930 DEG C, and finishing temperature control is at 900 DEG C；The total reduction of first paragraph rolling is 38%, and the total reduction of second stage is 75%, it is thus achieved that hot rolled steel plate；
With the cooling rate of 80 ~ 90 DEG C/s, hot rolled steel plate is cooled to 180 ± 20 DEG C, and then air cooling is to room temperature, it is thus achieved that low-carbon hot-rolling ultra-high-strength/tenacity steel, and yield strength is 970MPa, and it is 95.3J that-20 DEG C of low-temperature impacts absorb merit；Tensile strength is 1250MPa, and elongation percentage is 14.9%；It is organized as the heterogeneous structure of bainite, martensite and retained austenite.
Embodiment 5
Making strand by set component smelting, refine and cast, strand composition is by weight percentage containing C 0.10%, Si 1.5%, Mn 2.0%, Cr 0.7%, Mo 0.3%, P 0.004%, S 0.003%, and surplus is Fe；
Strand is reheated to austenitizing temperature, and heating and temperature control, at 1100 DEG C, is incubated 2.5 hours, is then forged into steel billet (forging by forging ratio 1.5) in 950 ~ 1050 DEG C of temperature ranges；
Heating steel billet to 1200 ± 10 DEG C being incubated 3 hours, carries out first stage rolling in austenite recrystallization district and austenite Unhydrated cement respectively and second stage rolls, the start rolling temperature of first stage is 1150 DEG C, and finishing temperature control is at 1120 DEG C；The start rolling temperature of second stage is 940 DEG C, and finishing temperature control is at 920 DEG C；The total reduction of first paragraph rolling is 35%, and the total reduction of second stage is 80%, it is thus achieved that hot rolled steel plate；
With the cooling rate of 70 ~ 80 DEG C/s, hot rolled steel plate is cooled to 180 ± 20 DEG C, and then air cooling is to room temperature, it is thus achieved that low-carbon hot-rolling ultra-high-strength/tenacity steel, and yield strength is 935MPa, and it is 108J that-20 DEG C of low-temperature impacts absorb merit；Tensile strength is 1190MPa, and elongation percentage is 16.6%；It is organized as the heterogeneous structure of bainite, martensite and retained austenite.
Claims (1)
1. the preparation method of a low-carbon hot-rolling ultra-high-strength/tenacity steel, it is characterised in that sequentially include the following steps:
(1) making strand by set component smelting, refine and cast, strand composition is by weight percentage containing C
0.10 ~ 0.11%, Si 1.35 ~ 1.5%, Mn 1.85 ~ 2.0%, Cr 0.7 ~ 0.8%, Mo 0.28 ~ 0.3%, P≤0.004%, S≤0.003%, surplus is Fe；Strand is reheated to austenitizing temperature, and heating and temperature control, at 1050 ~ 1100 DEG C, is incubated more than 2.5 hours, is then forged into steel billet in 950 ~ 1050 DEG C of temperature ranges；
(2) heating steel billet to 1200 ± 10 DEG C is incubated at least 2 hours, carry out first stage rolling in austenite recrystallization district and austenite Unhydrated cement respectively and second stage rolls, the start rolling temperature scope of first stage is 1130 ~ 1150 DEG C, and finishing temperature control is more than 1100 DEG C；The start rolling temperature scope of second stage is 930 ~ 950 DEG C, and finishing temperature control is between 900 ~ 930 DEG C；The total reduction of first paragraph rolling is 35 ~ 40%, and the total reduction of second stage is 75 ~ 80%, it is thus achieved that hot rolled steel plate；
(3) with the cooling rate of 60 ~ 90 DEG C/s, hot rolled steel plate being cooled to 180 ± 20 DEG C, then air cooling is to room temperature, it is thus achieved that low-carbon hot-rolling ultra-high-strength/tenacity steel；The yield strength of low-carbon hot-rolling ultra-high-strength/tenacity steel is 900 ~ 980MPa, and it is 86.8 ~ 117.8J that-20 C low-temperature impacts absorb merit.
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