CN102899584B - Method for reducing ductile-brittle transition temperature of martensitic high strength steel - Google Patents
Method for reducing ductile-brittle transition temperature of martensitic high strength steel Download PDFInfo
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- CN102899584B CN102899584B CN201210418506.5A CN201210418506A CN102899584B CN 102899584 B CN102899584 B CN 102899584B CN 201210418506 A CN201210418506 A CN 201210418506A CN 102899584 B CN102899584 B CN 102899584B
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Abstract
The invention relates to a method for reducing the ductile-brittle transition temperature of martensitic high strength steel, and belongs to the technical field of steel plate production. The steel comprises the following chemical components: C: 0.14 - 0.15%, Si: 0.20 - 0.25%, Mn: 1.0 - 1.1%, P: less than or equal to 0.02%, S: less than or equal to 0 .005%, Cr: 0.30 - 0.80%, Ni: 0.30 - 0.80%, Mo: 0.30 - 0.35%, Nb: 0.035 - 0.040%, Ti: 0.011 - 0.015%, B: 0.0010 - 0.0020%, and the balance being Fe and inevitable impurities. A zero insulation quenching process is adopted by the invention. Compared with the steel plate produced by the conventional insulation quenching process, the steel plate produced by the process has the advantages that the strength, the impact toughness and the hardness are substantially improved, especially the ductile-brittle transition temperature is reduced by above 20 DEG C. The production process has the advantages of simple process, short period, low degree of oxidation of the steel plate, low energy consumption and high production efficiency.
Description
Technical field
The invention belongs to Plate Production technical field, particularly a kind of method that reduces martensite high-strength steel ductile-brittle transition temperature.
Background technology
High-strength steel can be widely used in the industries such as mining machinery, coal fell and transport, agricultural machine, building machinery, transportation by railroad, along with all kinds of engineering machinery are towards the development of maximization, lightweight, high-parameters direction, the market demand of the high-grade steel plate of high strength increases gradually.(take bainite or sorbite as matrix) high-strength steel capability and performance of the 80kg that recent year iron and steel enterprise produces and following rank has had larger progress, substantially can meet the need of market.But for 100kg and above rank, the ultrahigh-strength steel plates take martensite as matrix, only have only a few enterprise to produce, but capability and performance has very large gap compared with external product, can not meet the need of market, and major part is dependence on import still.
Restriction martensite high-strength steel produces and a major cause of performance is the rising along with intensity, toughness variation, and especially, for other martensite high-strength steel of 1000MPa higher level, its toughness levels is lower.For example, patent CN1840723A, its yield strength reaches 1100MPa level, but its-20 ℃ of ballistic works are below 50J, and-40 ℃ of ballistic works are lower; Patent CN102181788A, its yield strength is 1100-1200MPa, but its product is roll bending, and-40 ℃ of ballistic works are also lower, and heat-treatment quenching soaking time is 20～90min, and the time is longer, and energy consumption is large.
If on the basis of current martensite high-strength steel, by suitable technique, do not reducing on the basis of its intensity plasticity, its toughness quality scale is risen to E level (40 ℃) and even F level (60 ℃) from D level (20 ℃), the use range that can increase substantially high-strength steel, its advantage will be more obvious.
Summary of the invention
The object of the invention is to propose a kind of method that reduces martensite high-strength steel ductile-brittle transition temperature, adopt zero insulation quenching technology, can make yield strength > 1100MPa, tensile strength > 1300MPa, unit elongation > 12%, the E level of Brinell hardness > 400HB and F level High Strength Steel Plate, compared with adopting the prepared steel plate of conventional time insulation quenching technology, the steel plate that this technique makes, its intensity, impelling strength, hardness all has certain amplitude to improve, especially ductile-brittle transition temperature reduces more than 20 ℃.
For achieving the above object, the present invention adopts following technical scheme:
The slab chemical composition (weight percent) that the present invention adopts: C:0.14～0.15%, Si:0.20～0.25%, Mn:1.0～1.1%, P≤0.02%, S≤0.005%, Cr:0.30～0.80%, Ni:0.30～0.80%, Mo:0.30～0.35%, Nb:0.035～0.040%, Ti:0.011～0.015%, B:0.0010～0.0020%, all the other are Fe and inevitable impurity.
Production technique of the present invention is as follows:
1), to above-mentioned heating of plate blank, Heating temperature is 1180～1220 ℃, soaking time 1.5～2.5h;
2) controlled rolling, cooling, roughing start rolling temperature≤1050 ℃, roughing finishing temperature >=990 ℃, pass deformation rate is 10～30%; 860～900 ℃ of finish rolling start rolling temperatures, finish rolling finishing temperature is 800～860 ℃, pass deformation rate is 10～30%; In controlled rolling process, overall compression ratio >=7, after finish to gauge, air cooling is to room temperature;
3) thermal treatment process: quenching temperature is 900～950 ℃, Quenching Soaking Time is 0min; Tempering temperature is 200～300 ℃, insulation 1～2h, air cooling after tempering.
The effect in the present invention of above-mentioned production technique is:
Step 1) in, as too low in slab heating temperature, the carbon of Nb, nitride can not dissolve completely; As too high in Heating temperature, Austenite Grain Growth, and slab oxidation aggravation, therefore Heating temperature is 1180～1220 ℃.As too short in heat-up time, austenitizing is inhomogeneous; Overlong time, slab oxidation is serious, and expends the energy, therefore soaking time is 1.5～2.5h.
Step 2) in, controlled rolling adopts the controlled rolling of two stages, and roughing is carried out more than recrystallization temperature Tnr, its objective is and makes austenite generation perfect recrystallization, with refine austenite crystal grain; Finishing rolling control, between Tnr and Ar3, its objective is and obtains the flat crystal grain with deformation bands, for subsequent heat treatment provides good forerunner's tissue.
Step 3) in, thermal treatment process adopts the technique of zero insulation quenching+tempering, and quenching temperature is got Ac3+50～100 ℃, and soaking time is zero.Because heat-up time is short, make austenite have little time to grow up, crystal grain is less, and homogenizing completely.The skewness of carbon and other alloying elements in austenite crystal microcell, the Ms point of different carbon concentration microcells is different.Low-carbon (LC) microcell Ms point is higher, first forms martensite in quench cooled process; High-carbon microcell Ms point is lower, rear generation martensite.Martensitic transformation has non-isothermal characteristic.Due to formation temperature difference, martensite plate can not pass through different carbon concentration districts and grow up, and therefore martensite has been obtained refinement.This refinement can make the performance of martensite high-strength steel obtain certain amplitude lifting.Tempering temperature is got 200～300 ℃, insulation 1～2h, and object is that martensite is decomposed, carbide precipitate is eliminated quenching internal stress simultaneously.
The present invention, owing to having adopted above technical scheme, makes it compared with prior art, at least has the following advantages and positively effect:
1, the present invention adopts zero insulation quenching technology.In steel plate hot treating processes, steel plate after temperature, without insulation, direct quenching.Therefore heat treatment cycle is short, and steel plate degree of oxidation is low, and energy consumption is low, and production efficiency is high.
2, adopt zero insulation quenching technology, the intensity of steel plate, toughness, hardness are compared compared with common process, have certain amplitude to improve, and ductile-brittle transition temperature reduces more than 20 ℃.
3, adopt zero insulation quenching technology, can make E level and the F level High Strength Steel Plate of yield strength > 1100MPa, tensile strength > 1300MPa, unit elongation > 12%, Brinell hardness > 400HB.
Accompanying drawing explanation
Fig. 1 is the microstructure picture in embodiment 1;
Fig. 2 is the microstructure picture in embodiment 2;
Fig. 3 is the microstructure picture in embodiment 3;
Fig. 4 is the microstructure picture in embodiment 4.
Embodiment
Below in conjunction with accompanying drawing and some preferred embodiments, technical scheme of the present invention is described in further detail, but is not limited to this.
Embodiment 1
This martensite high-strength steel (wt%) composed of the following components: C:0.14%, Si:0.25%, Mn:1.0%, P≤0.02%, S≤0.0050%, Cr:0.30%, Ni:0.30%, Mo:0.30%, Nb:0.035%, Ti:0.015%, B:0.0013%, all the other are Fe and inevitable impurity.
1), to above-mentioned heating of plate blank, Heating temperature is 1180～1220 ℃, soaking time 1.5～2.5h;
2) controlled rolling, cooling, roughing start rolling temperature≤1050 ℃, roughing finishing temperature >=990 ℃, pass deformation rate is 10～30%; 860～900 ℃ of finish rolling start rolling temperatures, finish rolling finishing temperature is 800～860 ℃, pass deformation rate is 10～30%; In controlled rolling process, overall compression ratio >=7, after finish to gauge air cooling to room temperature, the thick 15mm of finished product;
3) thermal treatment process: quenching temperature is 930 ℃, Quenching Soaking Time is 0min; Tempering temperature is 250 ℃, insulation 1～2h, air cooling after tempering.
The present embodiment obtains the mechanical property of steel plate in table 1.
Comparative example 1
Embodiment is as embodiment 1, and wherein Quenching Soaking Time is 60min.
This comparative example obtains the mechanical property of steel plate in table 1.
Embodiment 2
This martensite high-strength steel (wt%) composed of the following components: C:0.15%, Si:0.25%, Mn:1.05%, P≤0.02%, S≤0.0050%, Cr:0.78%, Ni:0.78%, Mo:0.35%, Nb:0.039%, Ti:0.015%, B:0.0019%, all the other are Fe and inevitable impurity.
1), to above-mentioned heating of plate blank, Heating temperature is 1180～1220 ℃, soaking time 1.5～2.5h;
2) controlled rolling, cooling, roughing start rolling temperature≤1050 ℃, roughing finishing temperature >=990 ℃, pass deformation rate is 10～30%; 860～900 ℃ of finish rolling start rolling temperatures, finish rolling finishing temperature is 800～860 ℃, pass deformation rate is 10～30%; In controlled rolling process, overall compression ratio >=7, after finish to gauge air cooling to room temperature, the thick 15mm of finished product;
3) thermal treatment process: quenching temperature is 930 ℃, Quenching Soaking Time is 0min; Tempering temperature is 200 ℃, insulation 1～2h, air cooling after tempering.
The present embodiment obtains the mechanical property of steel plate in table 1.
Comparative example 2
Embodiment is as embodiment 2, and wherein Quenching Soaking Time is 30min.
This comparative example obtains the mechanical property of steel plate in table 1.
Embodiment 3
Embodiment is as embodiment 2, and wherein tempering process is: tempering temperature: 250 ℃, and soaking time: 1～2h.
The present embodiment obtains the mechanical property of steel plate in table 1.
Comparative example 3
Embodiment is as embodiment 3, and wherein Quenching Soaking Time is 15min.
This comparative example obtains the mechanical property of steel plate in table 1.
Embodiment 4
Embodiment is as embodiment 3, and wherein tempering process is: tempering temperature: 300 ℃, and soaking time: 1～2h.
The present embodiment obtains the mechanical property of steel plate in table 1.
Comparative example 4
Embodiment is as embodiment 4, and wherein Quenching Soaking Time is 30min.
This comparative example obtains the mechanical property of steel plate in table 1.
The mechanical property of table 1 embodiment of the present invention 1-4 and comparative example 1-4
Note: in table 1, tension specimen adopts the bar-shaped sample that diameter phi 8mm, gauge length are 40mm, sample position is laterally sampling, thickness of slab 1/2 place; Charpy bar is of a size of 10 × 10 × 55mm, and sample position is longitudinally sampling, thickness of slab 1/2 place; HBW is 3mm place hardness under surface of steel plate, alloy steel ball diameter 10mm, test force 3000kgf, test force hold-time 10s.Ductile-brittle transition temperature (DBTT) is got temperature corresponding to impact specimen fracture 50% fiber section rate.
From table 1, adopt zero insulation quenching technology, its yield strength, tensile strength, hardness all obtain certain amplitude and improve, and ductile-brittle transition temperature DBTT at least reduces more than 21 ℃.
Claims (1)
1. one kind is reduced the method for martensite high-strength steel ductile-brittle transition temperature, the chemical composition of steel is by weight percentage: C:0.14～0.15%, Si:0.20～0.25%, Mn:1.0～1.1%, P≤0.02%, S≤0.005%, Cr:0.30～0.80%, Ni:0.30～0.80%, Mo:0.30～0.35%, Nb:0.035～0.040%, Ti:0.011～0.015%, B:0.0010～0.0020%, and all the other are Fe and inevitable impurity; It is characterized in that: production technique is:
1) smelt, be cast into slab according to above-mentioned chemical composition;
2), to above-mentioned heating of plate blank, Heating temperature is 1180～1220 ℃, soaking time 1.5～2.5h;
3) controlled rolling, cooling, roughing start rolling temperature≤1050 ℃, roughing finishing temperature >=990 ℃, pass deformation rate is 10～30%; 860～900 ℃ of finish rolling start rolling temperatures, finish rolling finishing temperature is 800～860 ℃, pass deformation rate is 10～30%; In controlled rolling process, overall compression ratio >=7, after finish to gauge, air cooling is to room temperature;
4) thermal treatment process, quenching temperature is 900～950 ℃, and Quenching Soaking Time is 0min, and tempering temperature is 200～300 ℃, insulation 1～2h, air cooling after tempering.
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| CN113215376B (en) * | 2021-04-28 | 2021-10-15 | 徐工集团工程机械股份有限公司科技分公司 | Loader bucket tooth and heat treatment method thereof |
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