CN104911501A - Super-strength high-carbon potential dislocation martensitic steel, and preparation method thereof - Google Patents
Super-strength high-carbon potential dislocation martensitic steel, and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a super-strength high-carbon potential dislocation martensitic steel, and a preparation method thereof. The super-strength high-carbon potential dislocation martensitic steel is composed of following chemical ingredients, 0.6 to 0.85% of C, 0.01 to 0.8% of Si, 0.1 to 0.5% of Mn, 0.8 to 2.0% of Cr, 0.05 to 0.4% of Cu, 0.05 to 0.3% of Ni, 0.02 to 0.1% of Ti, 0.02 to 0.2% of V, 0.02 to 0.15% of Nb, P<0.02%, S<0.02%, and the balance Fe. The preparation method comprises following steps: 1) raw material ingredients are subjected to smelting so as to obtain ingot casting; 2) the ingot casting is heated to 1100 to 1200 DEG C, is subjected to thermal insulation for 2h, and then forging or rolling so as to obtain a green body, and the green body is subjected to air cooling to room temperature; 3) the green body is heated to 500 to 700 DEG C, is subjected to thermal insulation for 1.5h, and then for rolling at a rolling reduction of 50 to 90%; 4) a product obtained via rolling is heated to 750 to 900 DEG C, is subjected to thermal insulation for 5 to 30min, and then quenching rapidly so as to cool the product to room temperature, and then is subjected to tempering at 160 to 350 DEG C so as to obtain the super-strength martensitic steel. Comprehensive mechanical properties of the super-strength martensitic steel are excellent; strength and plasticity are higher than that of most maraging steel; the preparation method is simple; and operation process is high in controllability.
Description
Technical field
The invention belongs to high-strength steel and prepare technical field, be specifically related to a kind of superstrength high-carbon dislocation type martensitic steel and preparation method thereof.
Background technology
Along with the development of modern industry, the Application Areas of ultrahigh-strength steel is constantly widened, and demand is increasing.High-alloy Ultra-high Strength Steel, as Secondery-hardening Ultrahigh Strength Steel such as AerMet100, AF1410,9Ni-4Co and 9Ni-4Co, and maraging steel, as 18Ni (250), 18Ni (300), Custom465, Custom475 etc., although have higher obdurability combination, but owing to making material cost expensive containing more expensive alloying elements Co, Ni and Mo etc., limit its Application Areas.Nanometer bainitic steel is the steel grade of new generation having high intensity levels grown up in recent years, and its ultimate tensile strength can reach 2.5GPa, and yield strength reaches 1.7GPa, and has good plasticity.But often to add expensive alloying elements Co in this steel, and need at a lower temperature long-time isothermal quenching a couple of days to the several months, make its production cycle long, cost is higher, and there is certain restriction to the size of material, be not suitable for doing large size material, in addition, nanometer bainite toughness when withstanding shocks load is poor, makes it apply and is restricted.
Therefore, the development trend that low cost ultrahigh-strength steel is following ferrous materials is researched and developed.C is the most effective one of element improving the strength of materials in steel, but carbon content general control is within 0.30wt.% in low-temperaturetempering martensitic steel, too high carbon can cause there is a large amount of twin crystal martensites in quenching structure, and the amount of twin crystal martensite can increase along with carbon content and increase, and causes the fragility of material to increase.Low-temperaturetempering medium high carbon martensite is often applied to withstanding shocks the less field of load, as cutlery, and mould, bearing etc.In current research in report, also fail to realize high carbon martensite being quenched and after low-temperaturetempering, obtaining the martensitic steel material of superstrength and plasticity.
Summary of the invention
The object of the present invention is to provide a kind of superstrength high-carbon dislocation type martensitic steel and preparation method thereof, the comprehensive mechanical property of the martensitic steel of this superstrength is good, and intensity and plasticity all exceed most of maraging steel; This preparation method's technique is simple, and operating process controllability is strong, can according to the austenite grain size size in heat treated temperature and time adjustment martensitic steel.
The present invention is achieved through the following technical solutions:
A kind of superstrength high-carbon dislocation type martensitic steel, by percentage to the quality, the chemical composition of this super-strength martensitic steel is: C:0.6% ~ 0.85%; Si:0.01% ~ 0.8%; Mn:0.1% ~ 0.5%; Cr:0.8% ~ 2.0%; Cu:0.05% ~ 0.4%; Ni:0.05% ~ 0.3%; Ti:0.02% ~ 0.1%; V:0.02% ~ 0.2%; Nb:0.02% ~ 0.15%; P:< 0.02%; S:< 0.02%, surplus is Fe.
The yield strength Rp of this superstrength high-carbon dislocation type martensitic steel
0.2be 1950 ~ 2250MPa, tensile strength Rm be 2150 ~ 2400MPa, unit elongation is 6 ~ 10%.
In this superstrength high-carbon dislocation type martensitic steel, original austenite average grain size is less than 10 μm; The microstructure of superstrength high-carbon dislocation type martensitic steel is perfect dislocation martensite or based on dislocation substructure martensite and with twins sub-structure martensite, wherein, the martensitic volume fraction of twins sub-structure controls within 20% of this microstructure.
A preparation method for superstrength high-carbon dislocation type martensitic steel, is characterized in that, comprise the following steps:
1) in the ratio of superstrength high-carbon dislocation type martensitic steel chemical composition described in claim 1, first raw steel, ferrochrome, ferrosilicon and the pig iron are heated to melting sources and become molten steel, vanadium iron, ferro-niobium, electrolytic nickel, fine copper, ferromanganese and titanium is added successively again in molten steel, insulation is until the homogenization of composition that adds, then be cast into steel ingot, pouring temperature is no more than 1550 DEG C;
2) be incubated 2h by behind Heating Steel Ingots to 1100 ~ 1200 DEG C, then carry out forging or rolling, obtain base substrate, air cooling is to room temperature;
3) be incubated 1.5h after base substrate being heated to 500 ~ 700 DEG C, then rolling, in the operation of rolling, draught is 50 ~ 90%;
4) by step 3) insulation 5 ~ 30min behind heating materials to 750 ~ 900 DEG C after process, be cooled to room temperature, then through 160 ~ 350 DEG C of temper 1 ~ 2.5h, obtain superstrength high-carbon dislocation type martensitic steel.
Step 2) be that ingot casting is made slab or pole through several times forging or rolling.
Step 2) carry out forging or the finish-forging of rolling or the temperature of finish to gauge are 800 ~ 900 DEG C.
Step 3) the operation of rolling be that point 2 ~ 5 passages complete.
Step 4) to be cooled to room temperature be by material cooling process in water or quenching oil.
Step 1) be become molten steel by being heated to melting sources in raw steel, ferrochrome, ferrosilicon and pig iron loading medium-frequency induction furnace.
Compared with prior art, the present invention has following useful technique effect:
1, the present invention adds element V, Ti and Nb of appropriate crystal grain thinning in the alloy, and control growing up of austenite grain size by the adjustment of Heating temperature in heat treatment process and soaking time, austenitic grain-size is made to control within 10 μm, the microstructure obtaining superstrength high-carbon dislocation type martensitic steel is perfect dislocation martensite or based on dislocation substructure martensite and with twins sub-structure martensite, the martensitic volume fraction of described twins sub-structure is within 20% of microstructure; Also allow to there is a small amount of undissolved carbide in microstructure.
2, the maximum pulling strength of superstrength high-carbon dislocation type martensitic steel of the present invention can reach 2.4GPa, and has the unit elongation of 10%, and the obdurability of material reaches the level of 18Ni (C350) maraging steel, and Rp
0.2>=1950Mpa, Rm>=2300MPa, unit elongation A>=6%, but the cost of material therefor is less than 1/100 of maraging steel cost.
Not containing expensive alloying elements in the chemical composition of 3, superstrength high-carbon dislocation type martensitic steel of the present invention, the cost of material is low, and preparation method's treatment process is simple, compared with existing super bainite isothermal quenching technique, this tempering process of quenching does not need to carry out long-time isothermal processes, and production efficiency is high, be easy to realize.
4, the application of superstrength high-carbon dislocation type martensitic steel of the present invention is not by the restriction of workpiece shapes, before the heat treatment materials processing can be become the workpiece of different shape, and then heat-treat, applied range.
Accompanying drawing explanation
Fig. 1 is the electromicroscopic photograph organized after the rolling of 1# material and after quenching;
Wherein, (a) is for organizing after 1# sample warm-rolling; B () is the Display of Grain Boundary after the thermal treatment of 1# sample; C () is tissue under the tem after the quenching of 1# sample;
Fig. 2 is the electromicroscopic photograph organized after the rolling of 2# material and after quenching;
Wherein, (a) is for organizing after 2# sample warm-rolling; B () is tissue under the tem after the quenching of 2# sample;
Fig. 3 is the electromicroscopic photograph organized after the rolling of 3# material and after quenching;
Wherein, (a) is for organizing after 3# sample warm-rolling; B () is tissue under the tem after the quenching of 3# sample;
Fig. 4 is the electromicroscopic photograph organized after the rolling of 4# material and after quenching;
Wherein, (a) is for organizing after 4# sample warm-rolling; B () is tissue under the tem after the quenching of 4# sample;
Fig. 5 is the electromicroscopic photograph organized after the rolling of 5# material and after quenching;
Wherein, (a) is for organizing after 5# sample warm-rolling; B () is tissue under the tem after the quenching of 5# sample
Fig. 6 is the electromicroscopic photograph organized after the rolling of 6# material and after quenching;
Wherein, (a) is for organizing after 6# sample warm-rolling; B () is tissue under the tem after the quenching of 6# sample.
Embodiment
Below in conjunction with specific embodiment, the present invention is described in further detail, and the explanation of the invention is not limited.
Superstrength high-carbon dislocation type martensitic steel chemical composition of the present invention is (wt.%): C:0.6 ~ 0.85, Si:0.01 ~ 0.8, Mn:0.1 ~ 0.5, Cr:0.8 ~ 2.0, Cu:0.05 ~ 0.4, Ni:0.05 ~ 0.3, Ti:0.02 ~ 0.1, V:0.02 ~ 0.2, Nb:0.02 ~ 0.15, P:< 0.02, S:< 0.02, surplus is Fe.
The superstrength high-carbon dislocation type martensitic steel of described composition adopts vacuum or ordinary method carry out melting and are cast into ingot casting; Then carry out forging or rolling after ingot casting being heated to 1100 ~ 1200 DEG C of insulation 2h, through multi-pass rolling or be forged into slab or pole, finish to gauge or final forging temperature control at 800 ~ 900 DEG C, and then air cooling is to room temperature; Carry out warm-rolling by after DEG C insulation 1.5h of heating materials to 500 ~ 700 after forging or rolling again, divide 2 ~ 5 passages to complete according to the scantling operation of rolling, draught is 50 ~ 90%.
Described superstrength high-carbon dislocation type martensitic steel is by adding element V, Ti, Nb of appropriate crystal grain thinning in the alloy, and controlling growing up of austenite grain size by the adjustment of Heating temperature in heat treatment process and soaking time, austenitic grain-size should control within 10 μm.In water or quenching oil, room temperature is cooled to rapidly after DEG C insulation 5 ~ 30min of heating materials to 750 after warm-rolling ~ 900, then at 160 ~ 350 DEG C of tempering 1 ~ 2.5h.
Perfect dislocation martensite is organized as or dislocation substructure martensite is lead and have a small amount of twins sub-structure martensite after the quenching of described superstrength high-carbon dislocation type martensitic steel, the volume fraction of twin crystal martensite should control within 20%, also allows a small amount of undissolved carbide in addition in tissue; Tempered martensite or tempered martensite and a small amount of undissolved carbide is organized as after tempered.
The steel of the present invention prepared according to above-mentioned chemical composition, treatment process and organizational controls technology not only has the tensile strength of superelevation, and also has good plasticity, and comprehensive mechanical property reaches 18Ni (C350) level.Specific performance is: Rp
0.2>=1950Mpa, Rm>=2300MPa, A>=6%.
Following Composition Design requirement according to the present invention devises the composition of 6 stove steel, and be numbered 1# ~ 6#, adopt electromagnetic induction furnace vacuum melting or ordinary method to carry out melting, be cast into Ф 100mm pole, the chemical composition of 6 stove steel is as shown in table 1.
Chemical composition composition (wt.%) of table 1 ultrahigh-strength steel
Embodiment 1
Forge after 1# sample after vacuum induction melting being heated to 1100 ~ 1200 DEG C of insulation 2h, being forged into thickness is 25mm heavy slab, and final forging temperature controls at 800 ~ 900 DEG C, and then air cooling is to room temperature; Carry out warm-rolling by after DEG C insulation 1.5h of the heating materials to 600 after forging again, the operation of rolling divides 3 passages to complete, and draught is 80%, and obtaining thickness is 5mm plate.After rolling material structure be nano-carbide Dispersed precipitate on ultra-fine ferrite matrix, as shown in Fig. 1 (a).Quenched rapidly in water after 850 DEG C of insulation 10min by material after rolling, the grain-size of original austenite is 4 ~ 7 μm, as shown in Fig. 1 (b), is organized as perfect dislocation substructure martensite, as shown in Fig. 1 (c) after quenching.Sample after quenching mechanical property after 160 DEG C of tempering 1h is: R
p0.2=2023MPa, R
m=2400MPa, A=10%.
Embodiment 2
Forge after 2# sample after ordinary method melting being heated to 1100 ~ 1200 DEG C of insulation 2h, be forged into Ф 40mm rod, final forging temperature controls at 800 ~ 900 DEG C, and then air cooling is to room temperature; Carry out warm-rolling by after DEG C insulation 1.5h of the heating materials to 700 after forging again, the operation of rolling divides 2 passages to complete, and draught is 50%, obtains Ф 20mm rod.After rolling material structure be nano-carbide Dispersed precipitate on ultra-fine ferrite matrix, as shown in Fig. 2 (a).Quenched rapidly in water after 800 DEG C of insulation 20min by material after rolling, the grain-size of original austenite is 4 ~ 6 μm, is organized as perfect dislocation substructure martensite, as shown in Fig. 2 (b) after quenching.Sample after quenching mechanical property after 200 DEG C of tempering 1.5h is: R
p0.2=1987MPa, R
m=2311MPa, A=7.2%.
Embodiment 3
Forge after 3# sample after ordinary method melting being heated to 1100 ~ 1200 DEG C of insulation 2h, be forged into Ф 45mm rod, final forging temperature controls at 800 ~ 900 DEG C, and then air cooling is to room temperature; Carry out warm-rolling by after DEG C insulation 1.5h of the heating materials to 550 after forging again, the operation of rolling divides 5 passages to complete, and draught is 90%, obtains Ф 5mm rod.After rolling material structure be nano-carbide Dispersed precipitate on ultra-fine ferrite matrix, as shown in Fig. 3 (a).Quenched rapidly in oil after 830 DEG C of insulation 15min by material after rolling, the grain-size of original austenite is 4 ~ 7 μm, organizes mainly dislocation substructure martensite after quenching, and the amount of twin crystal martensite is less than 10%, as shown in Fig. 3 (b).Sample after quenching mechanical property after 250 DEG C of tempering 2.5h is: R
p0.2=2052MPa, R
m=2407MPa, A=9.3%.
Embodiment 4
Be rolled after 4# sample after vacuum induction melting being heated to 1100 ~ 1200 DEG C of insulation 2h, rolling into thickness is 45mm heavy slab, and final forging temperature controls at 800 ~ 900 DEG C, and then air cooling is to room temperature; Warm-rolling is carried out again by after DEG C insulation 1.5h of the heating materials to 500 after rolling, the operation of rolling divides 3 passages to complete, and draught is 55%, and obtaining thickness is 20mm plate, after rolling material structure be nano-carbide Dispersed precipitate on ultra-fine ferrite matrix, as shown in Fig. 4 (a).Quenched rapidly in oil after 750 DEG C of insulation 30min by material after rolling, the grain-size of original austenite is 4 ~ 6 μm, is organized as dislocation substructure martensite after quenching, and has a small amount of undissolved carbide, as shown in Fig. 4 (b).Sample after quenching mechanical property after 200 DEG C of tempering 1.5h is: R
p0.2=2056MPa, R
m=2317MPa, A=6.7%.
Embodiment 5
Forge after 5# sample after vacuum induction melting being heated to 1100 ~ 1200 DEG C of insulation 2h, being forged into thickness is 40mm heavy slab, and final forging temperature controls at 800 ~ 900 DEG C, and then air cooling is to room temperature; Warm-rolling is carried out again by after DEG C insulation 1.5h of the heating materials to 650 after forging, the operation of rolling divides 5 passages to complete, and draught is 75%, and obtaining thickness is 10mm plate, after rolling material structure be nano-carbide Dispersed precipitate on ultra-fine ferrite matrix, as shown in Fig. 5 (a).Quenched rapidly in oil after 880 DEG C of insulation 20min by material after rolling, the grain-size of original austenite is 6 ~ 10 μm, organizes mainly dislocation substructure martensite after quenching, and the amount of twin crystal martensite is less than 15%, as shown in Fig. 5 (b).Sample after quenching mechanical property after 250 DEG C of tempering 2h is: R
p0.2=2127MPa, R
m=2412MPa, A=6.1%.
Embodiment 6
Forge after 6# sample after vacuum induction melting being heated to 1100 ~ 1200 DEG C of insulation 2h, being forged into thickness is 45mm heavy slab, and final forging temperature controls at 800 ~ 900 DEG C, and then air cooling is to room temperature; Carry out warm-rolling by after DEG C insulation 1.5h of the heating materials to 620 after forging again, the operation of rolling divides 5 passages to complete, and draught is 85%, and obtaining thickness is 5mm plate.After rolling material structure be nano-carbide Dispersed precipitate on ultra-fine ferrite matrix, as shown in Fig. 6 (a).Quenched rapidly in oil after 860 DEG C of insulation 12min by material after rolling, the grain-size of original austenite is 5 ~ 8 μm, organizes mainly dislocation substructure martensite after quenching, and the amount of twin crystal martensite is less than 20%, as shown in Fig. 6 (b).Sample after quenching mechanical property after 350 DEG C of tempering 1h is: R
p0.2=2176MPa, R
m=2426MPa, A=6%.
In sum, super-strength martensitic steel Central Plains of the present invention austenite grain size is less than 10 μm, microstructure after quenching is perfect dislocation martensite or dislocation substructure martensite is lead and have a small amount of twins sub-structure martensite, and the volume fraction of twin crystal martensite should be less than 20%; In addition, a small amount of undissolved carbide is also allowed in tissue.Super-strength martensitic steel of the present invention has good comprehensive mechanical property: Rp0.2 >=1950MPa, Rm >=2300MPa, A >=6%.
Production technique of the present invention is simple, and intensity and plasticity exceed most of maraging steel, and does not need in material to add a large amount of alloying elements, can greatly reduce costs.The steel adopting the present invention to prepare has superstrength, and can reach 18Ni (C350) level, material maximum pulling strength can reach 2.4GPa, and has the unit elongation of 10%.Not containing expensive alloying elements in material, the cost of material is low, and treatment process is simple, and compare with super bainite isothermal quenching technique, this tempering process of quenching does not need to carry out long-time isothermal processes, and production efficiency is high, be easy to realize.Materials processing, not by the restriction of workpiece shapes, can be become the workpiece of different shape, and then heat-treat, expand its range of application by the application of steel of the present invention before the heat treatment.
Claims (9)
1. a superstrength high-carbon dislocation type martensitic steel, is characterized in that, by percentage to the quality, the chemical composition of this superstrength high-carbon dislocation type martensitic steel is: C:0.6% ~ 0.85%; Si:0.01% ~ 0.8%; Mn:0.1% ~ 0.5%; Cr:0.8% ~ 2.0%; Cu:0.05% ~ 0.4%; Ni:0.05% ~ 0.3%; Ti:0.02% ~ 0.1%; V:0.02% ~ 0.2%; Nb:0.02% ~ 0.15%; P:< 0.02%; S:< 0.02%, surplus is Fe.
2. a kind of superstrength high-carbon dislocation type martensitic steel according to claim 1, is characterized in that, the yield strength Rp of this superstrength high-carbon dislocation type martensitic steel
0.2be 1950 ~ 2250MPa, tensile strength Rm be 2150 ~ 2400MPa, unit elongation is 6 ~ 10%.
3. a kind of superstrength high-carbon dislocation type martensitic steel according to claim 1, is characterized in that, in this superstrength high-carbon dislocation type martensitic steel, original austenite average grain size is less than 10 μm; The microstructure of superstrength high-carbon dislocation type martensitic steel is perfect dislocation martensite or based on dislocation substructure martensite and with twins sub-structure martensite, wherein, the martensitic volume fraction of twins sub-structure controls within 20% of this microstructure.
4. a preparation method for superstrength high-carbon dislocation type martensitic steel, is characterized in that, comprise the following steps:
1) in the ratio of superstrength high-carbon dislocation type martensitic steel chemical composition described in claim 1, first raw steel, ferrochrome, ferrosilicon and the pig iron are heated to melting sources and become molten steel, vanadium iron, ferro-niobium, electrolytic nickel, fine copper, ferromanganese and titanium is added successively again in molten steel, insulation is until the homogenization of composition that adds, then be cast into steel ingot, pouring temperature is no more than 1550 DEG C;
2) be incubated 2h by behind Heating Steel Ingots to 1100 ~ 1200 DEG C, then carry out forging or rolling, obtain base substrate, air cooling is to room temperature;
3) be incubated 1.5h after base substrate being heated to 500 ~ 700 DEG C, then rolling, in the operation of rolling, draught is 50 ~ 90%;
4) by step 3) insulation 5 ~ 30min behind heating materials to 750 ~ 900 DEG C after process, be cooled to room temperature, then through 160 ~ 350 DEG C of temper 1 ~ 2.5h, obtain superstrength high-carbon dislocation type martensitic steel.
5. the preparation method of a kind of superstrength high-carbon dislocation type martensitic steel according to claim 4, is characterized in that, step 2) be that ingot casting is made slab or pole through several times forging or rolling.
6. the preparation method of a kind of superstrength high-carbon dislocation type martensitic steel according to claim 4, is characterized in that, step 2) carry out forging or the finish-forging of rolling or the temperature of finish to gauge are 800 ~ 900 DEG C.
7. the preparation method of a kind of superstrength high-carbon dislocation type martensitic steel according to claim 4, is characterized in that, step 3) the operation of rolling be that point 2 ~ 5 passages complete.
8. the preparation method of a kind of superstrength high-carbon dislocation type martensitic steel according to claim 4, is characterized in that, step 4) to be cooled to room temperature be by material cooling process in water or quenching oil.
9. the preparation method of a kind of superstrength high-carbon dislocation type martensitic steel according to claim 4, is characterized in that, step 1) be become molten steel by being heated to melting sources in raw steel, ferrochrome, ferrosilicon and pig iron loading medium-frequency induction furnace.
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| CN105586536A (en) * | 2015-12-31 | 2016-05-18 | 西安交通大学 | High-strength high-tenacity layered structure low-carbon martensite steel and preparing method thereof |
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| CN112899445A (en) * | 2021-01-18 | 2021-06-04 | 山西太钢不锈钢股份有限公司 | Heat treatment method for super martensitic stainless steel medium plate |
| CN113151645A (en) * | 2021-04-14 | 2021-07-23 | 鞍钢集团北京研究院有限公司 | High-ductility maraging steel with excellent fatigue resistance and preparation method thereof |
| CN114717486A (en) * | 2021-08-25 | 2022-07-08 | 哈尔滨工程大学 | Ultra-high-strength high-performance maraging stainless steel and warm rolling preparation method thereof |
| CN114717486B (en) * | 2021-08-25 | 2023-09-19 | 哈尔滨工程大学 | Ultra-high-strength high-performance maraging stainless steel and warm rolling preparation method thereof |
| CN114774800A (en) * | 2022-04-19 | 2022-07-22 | 河南科技大学 | Ultrahigh-strength and high-ductility and toughness martensitic steel and preparation method thereof |
| CN114774800B (en) * | 2022-04-19 | 2023-08-08 | 河南科技大学 | Ultrahigh-strength high-plasticity and toughness martensitic steel and preparation method thereof |
| CN114774642A (en) * | 2022-04-25 | 2022-07-22 | 中航试金石检测科技(西安)有限公司 | Heat treatment process for A-100 steel |
| CN114774642B (en) * | 2022-04-25 | 2023-11-24 | 中航试金石检测科技(西安)有限公司 | Heat treatment process for A-100 steel |
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