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Low-carbon hot-rolled ultrahigh-strength high-toughness steel and preparation method thereof

A technology for ultra-high-strength and high-toughness steel, which is applied in the field of low-carbon hot-rolled ultra-high-strength and high-toughness steel and its preparation, can solve the problems of high cost, complicated process, and no significant improvement in production efficiency, and achieve high production efficiency and energy efficiency. The effect of low consumption and simple process control

Active Publication Date: 2015-03-25
NORTHEASTERN UNIV
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  • Abstract
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  • Application Information

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Problems solved by technology

[0003] The Chinese patent application with the application number 200510024756 discloses "an ultra-high-strength steel plate with a yield strength of 1100 MPa or more and its manufacturing method". This invention optimizes the traditional reheating quenching + tempering modulation process, but uses online quenching to shorten the process flow Improve production efficiency, but this method must carry out a tempering process. After the tempering process, the yield strength of the five examples is greater than 1100MPa, the elongation is greater than or equal to 13%, and the impact energy at -20°C is 36~47J; the application number is The Chinese patent application of 201110096170.0 and the Chinese patent application of application number 201410089398.0 both proposed the preparation process of quenching + low temperature tempering to obtain ultra-high-strength steel with a yield strength of 1100MPa or more, elongation between 11~15%, and -20 oC impact The work force is about 45J; it can be seen from the above comparative patents that although such patents have obtained high strength, they all inevitably adopt the tempering process, which does not significantly improve production efficiency
[0004] The Chinese patent application with application number 200610051936 discloses "1100MPa grade non-quenched and tempered high-strength steel and its production method". This invention requires a cold rolling process with a large reduction of 70-80% on the basis of hot rolling to obtain elongation. 1100MPa grade non-quenched and tempered high-strength steel with 10.5~12.5% ​​is still complicated in process and high in cost

Method used

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  • Low-carbon hot-rolled ultrahigh-strength high-toughness steel and preparation method thereof
  • Low-carbon hot-rolled ultrahigh-strength high-toughness steel and preparation method thereof

Examples

Experimental program
Comparison scheme
Effect test

Embodiment 1

[0025] Smelting, refining and pouring according to the set composition to make a slab, the composition of the slab contains C 0.10%, Si 1.43%, Mn 1.85%, Cr 0.7%, Mo 0.28%, P 0.003%, S 0.003%, balance The amount is Fe;

[0026] Reheat the billet to the austenitizing temperature, control the heating temperature at 1050°C, keep it warm for 2.5 hours, and then forge it into a billet within the temperature range of 950~1050°C (forging at a forging ratio of 1.7);

[0027] Heat the billet to 1200±10°C for 2 hours, and carry out the first-stage rolling and the second-stage rolling in the austenite recrystallization zone and the austenite non-recrystallization zone respectively, and the first-stage rolling temperature is 1130 ℃, the final rolling temperature is controlled at 1100 ℃; the starting rolling temperature of the second stage is 930 ℃, and the final rolling temperature is controlled at 900 ℃; The rate is 75%, and the hot-rolled steel plate is obtained;

[0028] Cool the hot-...

Embodiment 2

[0030] Smelting, refining and pouring according to the set composition to make slabs, the composition of slabs contains C 0.11%, Si 1.35%, Mn 1.89%, Cr 0.8%, Mo 0.29%, P 0.004%, S 0.002%, balance The amount is Fe;

[0031] Reheat the billet to the austenitizing temperature, control the heating temperature at 1080°C, keep it warm for 3 hours, and then forge it into a billet within the temperature range of 950~1050°C (forging at a forging ratio of 1.5);

[0032] Heat the billet to 1200±10°C for 3 hours, and carry out the first-stage rolling and the second-stage rolling in the austenite recrystallization zone and the austenite non-recrystallization zone respectively, and the first-stage rolling temperature is 1140 ℃, the final rolling temperature is controlled at 1110 ℃; the second-stage rolling start temperature is 940 ℃, and the final rolling temperature is controlled at 920 ℃; the total rolling reduction rate of the first stage rolling is 35%, and the second stage The rate is...

Embodiment 3

[0035] Smelting, refining and pouring according to the set composition to make slab, the composition of slab contains 0.10% C, 1.4% Si, 1.92% Mn, 0.7% Cr, 0.3% Mo, 0.001% P, 0.002% S, etc. The amount is Fe;

[0036] Reheat the billet to the austenitizing temperature, control the heating temperature at 1100°C, keep it warm for 2.5 hours, and then forge it into a billet in the temperature range of 950~1050°C (forging at a forging ratio of 1.7);

[0037] Heat the billet to 1200±10°C for 2.5 hours, and carry out the first-stage rolling and the second-stage rolling in the austenite recrystallization zone and the austenite non-recrystallization zone respectively, and the first-stage rolling temperature is 1150 ℃, the final rolling temperature is controlled at 1120 ℃; the second-stage rolling start temperature is 950 ℃, and the final rolling temperature is controlled at 930 ℃; The rate is 80%, and the hot-rolled steel plate is obtained;

[0038] Cool the hot-rolled steel plate at a...

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Abstract

A low-carbon hot-rolled ultrahigh-strength high-toughness steel and a preparation method thereof belong to the technical field of metallurgy. The low-carbon hot-rolled ultrahigh-strength high-toughness steel comprises the following ingredients by weight percent: 0.10-0.11 percent of C, 1.35-1.5 percent of Si, 1.85-2.0 percent of Mn, 0.7-0.8 percent of Cr, 0.28-0.3 percent of Mo, less than or equal to 0.004 percent of P, less than or equal to 0.003 percent of S and the balance of Fe, the yield strength is 900-980 MPa, and the impact absorbing energy at the low temperature of 20 DEG C below zero is 86.8-117.8 J. The preparation method comprises the following steps: (1) smelting, refining and casting to obtain casting blanks according to the set ingredients, re-heating the casting blanks to the austenitizing temperature, keeping the temperature for more than 2.5 hours, and forging at the temperature of 950-1050 DEG C to obtain billets; (2) heating up to 1190-1210 DEG C, keeping the temperature for at least 2 hours, and then performing air-cooling to the room temperature. The characteristics that the ingredients are reasonably designed and the process is simple, convenient and feasible in control are achieved; as on-line direct quenching is adopted, and no tempering procedure exists, the production efficiency is high, the energy consumption is low, and the obtained steel material has superhigh strength and favorable low-temperature ductility.

Description

technical field [0001] The invention belongs to the technical field of metallurgy, in particular to a low-carbon hot-rolled ultra-high-strength and high-toughness steel and a preparation method thereof. Background technique [0002] In recent years, with the rapid increase of high-strength structural parts and construction machinery and the deteriorating service environment, structural steel is developing towards higher strength and good low-temperature toughness. In order to reduce production costs and improve overall performance, especially to solve the contradiction between strength improvement and welding performance decline, on the premise of ensuring excellent low temperature toughness and welding performance, through appropriate and reasonable adjustment of alloy element content and further improvement of controlled rolling and controlled cooling process , can greatly improve the elongation and fracture toughness. [0003] The Chinese patent application with the appl...

Claims

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Application Information

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Patent Type & Authority Applications(China)
IPC IPC(8): C22C38/38C21D8/02
Inventor 谢辉胡军孙国胜高秀华吴红艳杜林秀
Owner NORTHEASTERN UNIV
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