CN101082101A - Chromic-nickel-free high-strength high ductility structural steel and manufacturing method thereof - Google Patents
Chromic-nickel-free high-strength high ductility structural steel and manufacturing method thereof Download PDFInfo
- Publication number
- CN101082101A CN101082101A CN 200610027019 CN200610027019A CN101082101A CN 101082101 A CN101082101 A CN 101082101A CN 200610027019 CN200610027019 CN 200610027019 CN 200610027019 A CN200610027019 A CN 200610027019A CN 101082101 A CN101082101 A CN 101082101A
- Authority
- CN
- China
- Prior art keywords
- steel
- nickel
- chromic
- structural steel
- strength
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The high strength and high toughness structural steel without Cr and Ni consists of C 0.24-0.30 wt%, Si 1.10-1.40 wt%, Mn 1.30-1.70 wt%, Mo 0.40-0.60 wt%, V 0.20-0.35 wt%, Al 0.015-0.050 wt%, Cu not more than 0.30 wt%, S not more than 0.012 wt%, P not more than 0.020 wt%, and Fe and inevitable impurities for the rest. Its production process includes the following steps: 1. smelting and casting ingot; 2. rolling in the heating temperature 1100-1180 deg.c, finishing temperature of 850-900 deg.c and cooling rate of 40-80 deg/hr; and 3. annealing at the temperature of 720+/-10 deg.c for 8-10 hr, cooling to below 450 deg.c in the rate no higher than 30 deg/hr and discharging. The high strength and high toughness structural steel with cheap Si and Mn as main elements has yield strength not lower than 1170 MPa, tensile strength not lower than 1274 MPa, specific elongation not lower than 9 %, reduction of area not lower than 45 %, and impact toughness not lower than 62J.
Description
Technical field
The present invention relates to the composition design and the manufacture method thereof of metallurgy industry structure iron, refer in particular to the composition design and the manufacture method thereof of high strength, high-toughness structural steel.
Background technology
Structure iron is common steel alloy.Press chromium, nickel element content in the steel, we tentatively can be divided into and contain chromium nickel structure iron, Chrome-free nickel structure iron (Chrome-free nickel type structure iron mainly is divided into 8 classes such as manganese steel, silicon manganese steel, boron steel, manganese boron steel, manganese molybdenum boron steel, manganese vanadium boron steel, vanadium steel, silicomanganese molybdenum-vanadium steel) two big classes.High strength, high-toughness structural steel generally are meant the structure iron of intensity 〉=1200Mpa, impelling strength Aku 〉=60J.
(intensity 〉=1200Mpa, impelling strength Aku 〉=60J) are broad-spectrum structure iron for high strength, high-toughness structural steel, as (needle-valve body idol part is the precise part of a key of diesel fuel system, and the quality of its quality directly has influence on the performance characteristics and the work-ing life of locomotive to be used for oil engine needle-valve body idol part.Needle-valve body is up to 250～270kg/cm
2The oil pressure effect under, needle-valve in valve body with the frequency of thousands of bobs of per minute, reach the fuel oil purpose of supplying with uniform atomizing, be subjected to the cylinder operation Temperature Influence simultaneously, the head temperature of needle-valve body can reach 270～360 ℃, so require needle-valve body should have high surface hardness, high-wearing feature, good anti-tempered performance, good dimensional stability and contact fatigue property with steel; And because the manufacturing process elaborate of needle-valve body, technical process is long, also requires material to have good machinability and grinding performance and certain solidity to corrosion.) high strength chromium nickel converted steel (common high strength, high-toughness structural steel).
At present, (intensity 〉=1200Mpa, impelling strength Aku 〉=60J), be to contain chromium nickel structure iron are as high strength converted steel (R to satisfy the high strength, high-toughness structural steel of oil engine needle-valve body idol part service requirements
m〉=1200Mpa), the trade mark commonly used be 20Cr2Ni4A, 18Cr2Ni4WA, 15CrMn2SiMo etc. (see Table 1, table 2 composition, performance comparison.)。Its deficiency is: chromium nickel content height makes the material price costliness, and machinability is poor simultaneously, and working (machining) efficiency is low, also need implement complicated heat treatment technology in order to reduce remained austenite content, poor dimensional stability, anti-temper resistance instability is general only 200 ℃ of left and right sides tempering.Therefore, still can not adapt to oil engine to high-speed boosting, the needs that the high-power direction develops.
Several groups of chromium nickel of table 1 converted steel composition contrast (wt%)
| Grade of steel | C | Mn | Si | Cr | Ni | V | W | Mo |
| 18Cr2Ni4WA | 0.13～ 0.19 | 0.30～ 0.60 | 0.20～ 0.40 | 1.35～ 1.65 | 4.00～ 4.50 | -- | 0.80～ 1.20 | -- |
| 20Cr2Ni4A | 0.17～ 0.24 | 0.30～ 0.60 | 0.20～ 0.40 | 1.25～ 1.75 | 3.25～ 3.75 | -- | -- | -- |
| 15CrMn2SiMo | 0.13～ 0.19 | 2.00～ 2.40 | 0.40～ 0.70 | 0.40～ 0.70 | -- | -- | -- | 0.40～ 0.50 |
Several groups of chromium nickel of table 2 converted steel performance and thermal treatment process contrast
| The trade mark | Thermal treatment process | Tensile strength R m(Mpa) | Yield strength R e，Mpa | Elongation A% | Relative reduction in area Z, % | Impelling strength, Aku, J |
| 18Cr2Ni4W A | For the first time quench 950 ± 15 ℃, for the second time quench 850 ± 15 ℃, 200 ± 20 ℃ of tempering | ≥1200 | ≥850 | ≥10 | ≥45 | ≥78 |
| 20Cr2Ni4A | For the first time quench 880 ± 15 ℃, for the second time quench 780 ± 15 ℃, 200 ± 20 ℃ of tempering | ≥1200 | ≥1100 | ≥10 | ≥45 | ≥63 |
| 15CrMn2Si Mo | Quench 860 ± 15 ℃ 200 ± 20 ℃ of tempering | ≥1200 | ≥900 | ≥10 | ≥45 | ≥63 |
From existing Chrome-free nickel type structure iron, the tensile strength of 7 class Chrome-free nickel type structure iron such as manganese steel, silicon manganese steel, boron steel, manganese boron steel, manganese molybdenum boron steel, manganese vanadium boron steel, vanadium steel generally can not surpass 1200Mpa, even intensity surpasses 1200Mpa, impelling strength yet very low (such as the ballistic work of spring steel generally below 20J) does not therefore belong to the category of high strength, high-toughness structural steel.Existing silicomanganese molybdenum vanadium class Chrome-free nickel type structure iron is aspect combination of strength and toughness, though good performance is arranged referring to (1) Yin Ruiyu " the modern progress-special steel of the quality of steel " volume two, metallurgical industry press, June nineteen ninety-five; (2) national standard: steel alloy handbook data storehouse electronic edition standard No. GB/T3077-1999:(3).Find: the Chrome-free nickel type structure iron that meets high strength, high-toughness structural steel performance index is the silicomanganese molybdenum-vanadium steel, it mainly comprises 20SiMn2MoV, 25SiMn2MoV, 37SiMn2MoV etc., the correlation data of steel grades, mechanical property and thermal treatment process sees table 1 and table 2 for details.), still, (still there is gap in the standard of intensity 〉=1200Mpa, impelling strength Aku 〉=62J) for the high strength that needs with oil engine needle-valve body idol part, the obdurability of high-toughness structural steel.
The no chromium nickel steel composition contrast of table 3 (wt%)
| Grade of steel | C | Si | Mn | Mo | V |
| 20SiMn2MoV | 0.17～0.23 | 0.90～1.20 | 2.20～2.60 | 0.30～0.40 | 0.05～0.12 |
| 25SiMn2MoV | 0.22～0.28 | 0.90～1.20 | 2.20～2.60 | 0.30～0.40 | 0.05～0.12 |
| 30SiMn2MoV | 0.27～0.33 | 0.40～0.70 | 1.60～1.90 | 0.40～0.50 | 0.15～0.25 |
| 37SiMn2MoV | 0.33～0.39 | 0.60～0.90 | 1.60～1.90 | 0.40～0.50 | 0.05～0.12 |
| 25SiMnMoV | 0.23～0.29 | 0.80～1.20 | 0.90～1.30 | 0.25～0.40 | 0.07～0.15 |
No chromium nickel steel performance of table 4 and thermal treatment process contrast
| The trade mark | Thermal treatment process | Tensile strength R m，Mpa | Yield strength R e，Mpa | Elongation A % | Relative reduction in area Z, % | Impelling strength, Aku, J |
| 20SiMn2MoV | Quench 900 ℃ 200 ℃ of tempering | ≥1380 | -- | ≥10 | ≥45 | ≥55 |
| 25SiMn2MoV | Quench 900 ℃ 200 ℃ of tempering | ≥1470 | -- | ≥10 | ≥40 | ≥47 |
| 30SiMn2MoV | Quench 900 ℃ 650 ℃ of tempering | ≥1000 | ≥800 | ≥12 | ≥50 | ≥78 |
| 37SiMn2MoV | Quench 900 ℃ 650 ℃ of tempering | ≥980 | ≥835 | ≥12 | ≥50 | ≥63 |
| 25SiMnMoV | Quench 900 ℃ 650 ℃ of tempering | ≥980 | ≥882 | ≥10 | ≥45 | ≥50 |
Chinese patent application CN95104296.3 discloses a kind of large section that high strength, high tenacity are provided of being applicable to structural part and steel plate, its chemical ingredients (weight %) is: carbon: 0.20～0.25%, silicon: 0.40～0.60%, manganese: 1.80～2.30%, molybdenum: 0.30～0.50%, tungsten: 0.40～0.60%, surplus is Fe.
But there is following deficiency in above-mentioned existing Chrome-free nickel type structure iron technology:
20SiMn2MoV, 25SiMn2MoV steel all adopt lower carbon content and relative high manganese content (2.20～2.60%), its objective is the deficiency that remedies intensity with manganese, but the manganese too high levels can tend to make austenite crystal thick in converted steel, cause flexible on the low side, so these two kinds of steel only are applicable to the less demanding purposes of impact toughness value.The carbon content of 30SiMn2MoV, 37SiMn2MoV steel employing 0.27～0.39% is come proof strength, but the converted steel carbon content is unfavorable for carburizing greater than 0.30%, and low simultaneously silicon, manganese content make the intensity of above-mentioned two steel can not reach more than the 1280Mpa far away.25SiMnMoV and invention steel have comparatively approaching carbon, silicone content, but manganese content is low excessively, are unfavorable for improving carburizing steel core portion perviousness, and the carbon that this steel is low relatively, silicon, manganese content have determined the strength level that it is lower.
More than the chemical ingredients of five steel determined its tissue, determining its mechanical property again indirectly, this mechanical property all can not satisfy the requirement of oil engine needle-valve body idol part.
Summary of the invention
The objective of the invention is to design a kind of high strength, high-toughness structural steel that does not contain chromium, nickel element, substitute existing high strength chromium nickel converted steel, it adopts cheap silicomanganese as main element, design and implement concrete technical scheme by the alloying composition, make steel reach the mechanical property of oil engine needle-valve body idol part requirement: yield strength 〉=1170MPa, tensile strength 〉=1274MPa, unit elongation 〉=9%, relative reduction in area 〉=45%, impelling strength 〉=62J.Solve chromium nickel converted steel and cost an arm and a leg, machinability is poor, and working (machining) efficiency is low, and defectives such as anti-tempering ability satisfy the requirement of diesel locomotive needle-valve body steel better.
The present invention adopts cheap Si, Mn as main element, uses no or little noble element, and the size of austenitic homogeneity and grain fineness number is controlled in control and optimize Si, Mn content, makes the finished steel performance reach the good toughness and tenacity of coupling.Make the invention steel have more stable anti-tempering ability, good machinability simultaneously.
Chromic-nickel-free high-strength high ductility structural steel of the present invention, its chemical element composition (weight %): carbon: 0.24～0.30%, silicon: 1.10～1.40%, manganese: 1.30～1.70%, molybdenum: 0.40～0.60%, vanadium: 0.20～0.35%, aluminium: 0.015～0.050%, copper≤0.30%, sulphur≤0.012%, phosphorus≤0.020%, all the other are iron and inevitable impurity.
Further, this structure iron is organized as ferrite+globular pearlite.
Wherein, carbon: be the principal element that improves hardness of steel, guarantee the necessary certain carbon content of certain intensity, but carbon be unfavorable to plasticity, simultaneously unfavorable to carburizing greater than 0.30% carbon content, control 0.24～0.30% carbon content is comparatively reasonable.
Manganese: replace carbon, chromium to keep intensity with manganese.Manganese is the principal element that can significantly improve hardening capacity, and manganese can suppress the formation of bainite in the cementation zone simultaneously; But manganese has the austenitizing of promotion grain growth shortcoming in steel, the content of manganese is controlled at 1.30～1.70% can bring into play good effect in steel of the present invention.
Silicon: silicon can reduce the concentration gradient of carbon in steel, promotes the carbon diffusion under austenitic state, and it can suppress separating out of carbide, helps the formation of cementation zone, and 1.10～1.40% improve toughness when can play solution strengthening.
Molybdenum: molybdenum act on highly significant in the steel, it not only can improve the hardening capacity of part cementation zone and heart portion, obviously suppresses the formation of non-martensite, can also improve piece surface hardness.But molybdenum element belongs to noble element, and the molybdenum of steel adding 0.40～0.60% of the present invention is most economical effective content.
Vanadium, aluminium all belong to the crystal grain thinning element.Aluminium, v element cooperate further crystal grain thinning with above-mentioned element, increase hardening capacity, and improve obdurability.But experience shows that too much vanadium is unfavorable to toughness, and too much aluminium easily increases the chance that steel inclusion produces, and therefore, 0.20～0.35% vanadium and 0.015～0.050% aluminium are the suitable content of steel of the present invention.
Simultaneously, sulphur, phosphorus, lead, antimony, bismuth should reduce its content as far as possible under technical qualification permission situation, to reduce the poly-partially of original austenite crystal prevention place, improve toughness.Residual element and gas content are controlled at suitable low levels level, make steel have quite high purity, are dissolved in and reach the best proportioning content of ideal between carbon in the austenite and each element, thereby lay a good foundation for the homogeneity and the obdurability that improve material.
The manufacture method of chromic-nickel-free high-strength high ductility structural steel of the present invention, it comprises the steps:
1) smelts, pours into a mould ingot, arc melting routinely, refinery practice, cast ingot;
2) rolling, 1100～1180 ℃ of hot rolling Heating temperatures, 1 hour 50 minutes～2 hours 10 minutes heat-up time, conventional silicomanganese molybdenum-vanadium steel soaking time is greater than 1 hour 20 minutes,
Technical solution of the present invention prolongs 30～50 minutes, to guarantee the steel billet homogeneous heating; 850～900 ℃ of finishing temperatures are rolled the back and are cooled off with 40～80 ℃/h speed of cooling;
3) stocking annealing, 720 ± 10 ℃ of annealing temperatures, soaking time 8～10 hours, with the speed of cooling that is not more than 30 ℃/h be as cold as≤450 ℃ come out of the stove.The conventional structure steel is lower than A for the elimination internal stress only need be heated to
C1The low temperature of (600～700 ℃), cold or the air cooling of stove gets final product behind even heat penetration, the technical program adopts 720 ± 10 ℃ of higher annealing temperatures, can shorten annealing time, to obtain globular pearlite+ferritic balanced weave is the best, can reduce simultaneously steel hardness and guarantee cutting ability, further crystal grain thinning.
Further, adopt electroslag remelting technique to improve the steel clarity in the step 1), improve the tissue of strand;
The present invention of cast ingot postcooling preferably substituted annealing in cold 16～24 hours with mould, prevented the tendency of ingot cracking, was not electroslag remelting process down together even the small cracking of steel ingot appearance also can not influence.
Step 2) it is cold that the hot rolling postcooling adopts case.
Again, bar is through ℃ tempering modifier treatment of 870～920 ℃ of oil quenching+200～350, and metallographic structure is a tempered martensite, has good mechanical property: yield strength 〉=1170MPa, tensile strength 〉=1274MPa, unit elongation 〉=9%, relative reduction in area 〉=45%, impelling strength 〉=62J.
In steel ingot or steel billet cooling, adopt slow cooling or annealing process to prevent steel ingot or steel billet cracking.
Beneficial effect of the present invention:
1. steel of the present invention reduces and has produced cost without chromium nickel and tungsten noble element, is the resource-conserving material, meets the trend of Sustainable development.
2. steel matter of the present invention is even, and hardness is moderate, has good machinability.
3. steel of the present invention has good hardening capacity and anti-tempered performance, can stand 250～350 ℃ of low-temperaturetemperings, so thermal treatment process is simple and direct, and quality is easy to control.
4. steel of the present invention is quenched and is had good comprehensive matching mechanical property: yield strength 〉=1170MPa, tensile strength 〉=1274MPa, unit elongation 〉=9%, relative reduction in area 〉=45%, impelling strength 〉=62J after the tempering.
Embodiment
Certain Iron And Steel Company implements patent of the present invention, smelts 26 electroslag heat (batch) numbers, its preparation method employing four step rule technical process: the first step: electric arc furnace just refines → the ladle furnace vacuum refinement → water the electrode ingot; Second step: esr; The 3rd step: rolling the becoming a useful person of rolling mill (blooming mill) hot-work; The 4th step: stocking annealing.
The first step, electric arc furnace smelting cast ingot
Adopt the white slag method, in 20～100 tons electric arc furnace, carry out molten steel and just refine, smelt the qualified substantially steel of composition, on AC system ladle refining furnace (capacity and electric furnace are complementary), carry out the refining of molten steel, remove obnoxious flavour and inclusion in the steel, the vacuum and the degassing; Cast electrode billet, cold 16～24 hours of electrode circle ingot mould (according to steel ingot billet size control mould cool time), the demoulding enters next procedure.
Generally adopt annealing process for the silicomanganese molybdenum-vanadium steel: steel ingot advances stove for about 600 ℃, is not more than the heat-up rate to 650 ℃ of 100 ℃/h ± 10 ℃ insulation 8 hours, and the cooling rate that is not more than 50 ℃/h is come out of the stove to about 450 ℃.
Second step, esr
1. preparation starting material
Slag charge will fully toast T 〉=600 ℃, storing time T 〉=4 hour.The striking agent is by proportioning Ti0
2: CaF
2=1: 1, lumpiness is even, is difficult for excessive.
2. melting is prepared
The crystallizer inner wall smooth is smooth, and waterworks is normal, places Dummy plate and striking agent.Settle crystallizer, the lifting consumable electrode.
3. reflow operation:
3.1 slag system: CaF
2: Al
2O
3=70: 30, striking agent, the melt cinder starting the arc.The quantity of slag: 70Kg.
3.2 energisingization slag technology:
Change slag: voltage 56～62V, electric current 2000～5000A, 20 minutes time
Electricity system: voltage 61～65V, electric current 12500～13500A
Bind: voltage 56～62V, electric current progressively reduces, time 〉=30 minute
3.3 normal remelting
Holding current is stable, and fluctuation range is controlled at ± 200A.
3.4 sampling, feeding
The length that should keep consumable electrode during sampling guarantees the feeding time, and the rising electrode cuts off high-voltage when getting glass sample, send high-voltage after the sampling earlier, back decline electrode, sampling back feeding begin to keep normal process regulation power in 2～3 minutes, change the feeding technology electric current then over to.
4. the demoulding: mould demoulding after cold 45 minutes, advance coldly behind stay-warm case slow cooling 〉=48 hour to send annealing furnace annealing.The general ambiguous time of silicomanganese molybdenum-vanadium steel is 36 hours, and technology of the present invention is according to different crystallizer size block cover half cool time 〉=48 hours, prevents that the influence of electroslag ingot cracking from producing.
5. electroslag ingot annealing: adopt 250～400 ℃ and advance stove, rise to 650～720 ℃, be incubated 10～12 hours, be cooled to≤450 ℃ of air coolings of coming out of the stove with≤30 ℃/h cooling rate with≤50 ℃/h heat-up rate.The annealing soaking time of general silicomanganese molybdenum-vanadium steel is 8 hours, and technical solution of the present invention has increased by 2～4 hours, has stipulated stove and tapping temperature simultaneously, with the assurance is to obtain the stabilized uniform annealed structure.
The 3rd step: rolling bar
Adopt rolling mill (blooming mill) hot-work rolling method, earlier qualified steel ingot rolling-cogging become billet, again billet hot-work is rolling to the finished product bar,
Breaking down, breaking down cogging technics rolling-cogging routinely, blooming mill hot-work is made billet with Rolling from Ingot:
1. process furnace heating process: 900 ℃ of insulations of steel ingot charging temperature 20～40 minutes; Be warming up to 1250～1260 ℃ in 3 hours 30 minutes; Be incubated 2 hours 30 minutes～3 hours; (conventional silicomanganese molybdenum-vanadium steel breaking down cogging soaking temperature is about 1290 ℃, and soaking time 1 hour 50 minutes, technical solution of the present invention are compared soaking temperature with prior art and reduced by 30～40 ℃, and soaking time prolongs 50～80 minutes, makes the full and uniform diffusion of steel ingot).
2. blooming mill rolling technology: rolling technology routinely, blooming mill becomes billet with qualified steel ingot rolling-cogging;
3. steel billet advanced the burial pit cooling more than 36 hours, and cold blank carries out sand stripping finishing.(conventional silicomanganese molybdenum-vanadium steel rolls the general annealing process that adopts in back, and the laggard burial pit slow cooling of technical solution of the present invention regulation steel billet whole stake cooling in heap is more than 36 hours, prevent to ftracture and reduce the content of hydrogen in the steel).Rolling mill hot-work with billet rolling to bar;
4. rolling mill process furnace heating process: 1100～1180 ℃ of Heating temperatures, 1 hour 50 minutes～2 hours 10 minutes heat-up time, the square billet male and female face temperature difference≤40 ℃ of steel billets are come out of the stove.
5. common process is rolling, 800～900 ℃ of finishing temperatures.
6. it is cold that steel roll back employing case, 40～80 ℃/h of speed of cooling.Conventional silicomanganese molybdenum-vanadium steel rolls back wind sheltering cooling in heap, and the present invention preferably adopts case cold, can effectively prevent the steel cracking.
The 4th step: stocking annealing
Softening annealing temperature: 720 ± 10 ℃; Soaking time 〉=8～10 hour, with the speed of cooling that is not more than 30 ℃/h be as cold as≤450 ℃ come out of the stove.
The chemical ingredients of table 3 embodiment rod iron, wt%
| Embodiment | C | S | P | Mn | Si | V | Ni | Cu | Al | Mo |
| 1 | 0.24 | 0.002 | 0.012 | 1.70 | 1.38 | 0.31 | 0.07 | 0.30 | 0.039 | 0.52 |
| 2 | 0.25 | 0.002 | 0.012 | 1.53 | 1.40 | 0.30 | 0.07 | 0.10 | 0.035 | 0.50 |
| 3 | 0.25 | 0.012 | 0.020 | 1.48 | 1.30 | 0.20 | 0.11 | 0.13 | 0.015 | 0.60 |
| 4 | 0.26 | 0.002 | 0.010 | 1.34 | 1.21 | 0.31 | 0.07 | 0.19 | 0.035 | 0.51 |
| 5 | 0.27 | 0.003 | 0.013 | 1.62 | 1.22 | 0.35 | 0.08 | 0.20 | 0.040 | 0.40 |
| 6 | 0.28 | 0.004 | 0.008 | 1.30 | 1.12 | 0.23 | 0.06 | 0.12 | 0.045 | 0.55 |
| 7 | 0.29 | 0.003 | 0.012 | 1.45 | 1.15 | 0.28 | 0.07 | 0.09 | 0.029 | 0.53 |
| 8 | 0.30 | 0.002 | 0.009 | 1.43 | 1.10 | 0.26 | 0.08 | 0.11 | 0.050 | 0.48 |
The mechanical property of table 4 embodiment rod iron
| Embodiment | Thermal treatment process | Tensile strength Rm (Mpa) | Yield strength Re, Mpa | Elongation A% | Relative reduction in area Z, % | Impelling strength, Aku.J | ||
| 1 | Quench: 890 ± 10 ℃, be incubated 45 minutes, oil cooling; Tempering: 280 ± 20 ℃, be incubated 150 minutes, air cooling. | 1400 | 1280 | 14.5 | 52.5 | 84 | 76 | 72 |
| 2 | 1610 | 1380 | 14.0 | 52.6 | 90 | 84 | 75 | |
| 3 | 1360 | 1240 | 14.5 | 54.0 | 94 | 72 | 66 | |
| 4 | 1380 | 1260 | 16.0 | 51.0 | 68 | 70 | 70 | |
| 5 | 1470 | 1350 | 17.0 | 55.0 | 96 | 80 | 96 | |
| 6 | 1350 | 1230 | 16.5 | 52.5 | 72 | 65 | 72 | |
| 7 | 1480 | 1360 | 14.2 | 51.5 | 88 | 89 | 98 | |
| 8 | 1460 | 1340 | 14.0 | 50.5 | 77 | 65 | 80 | |
Implement the Steel Bar During that the present invention produces, be applied to the fuel injection valve for internal combustion engines needle-valve body through domestic certain petrol pump factory's deep processing, every performance all meets service requirements.The demand of fuel injection valve for internal combustion engines needle-valve body material has been satisfied in example evidence, the present invention.
Claims (7)
1. chromic-nickel-free high-strength high ductility structural steel, its composition quality per-cent: carbon: 0.24～0.30%, silicon: 1.10～1.40%, manganese: 1.30～1.70%, molybdenum: 0.40～0.60%, vanadium: 0.20～0.35%, aluminium: 0.015～0.050%, copper≤0.30%, sulphur≤0.012%, phosphorus≤0.020%, Yu Weitie and inevitable impurity.
2. chromic-nickel-free high-strength high ductility structural steel as claimed in claim 1 is characterized in that this structure iron is organized as ferrite+globular pearlite.
3. the manufacture method of chromic-nickel-free high-strength high ductility structural steel as claimed in claim 1, it comprises the steps:
1) smelts, pours into a mould ingot, arc melting routinely, refinery practice, cast ingot;
2) rolling, the hot rolling Heating temperature is 1100～1180 ℃ behind the steel ingot cogging, and 1 hour 50 minutes～2 hours 10 minutes heat-up time, 850～900 ℃ of finishing temperatures are rolled the back and cooled off with 40～80 ℃/h speed of cooling;
3) stocking annealing, 720 ± 10 ℃ of annealing temperatures, soaking time 8～10 hours, with the speed of cooling that is not more than 30 ℃/h be as cold as≤450 ℃ come out of the stove.
4. the manufacture method of chromic-nickel-free high-strength high ductility structural steel as claimed in claim 3 is characterized in that, adopts electroslag remelting technique in the step 1).
5. the manufacture method of chromic-nickel-free high-strength high ductility structural steel as claimed in claim 4, it is characterized in that, the annealing of step 1) electroslag ingot, adopt 250～400 ℃ and advance stove, rise to 650～720 ℃ with≤50 ℃/h heat-up rate, be incubated 10～12 hours, be cooled to≤450 ℃ of air coolings of coming out of the stove with≤30 ℃/h cooling rate.
6. the manufacture method of chromic-nickel-free high-strength high ductility structural steel as claimed in claim 3 is characterized in that, step 1) cast ingot postcooling adopts mould cold.
7. the manufacture method of chromic-nickel-free high-strength high ductility structural steel as claimed in claim 3 is characterized in that step 2) roll postcooling and adopt case cold.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2006100270190A CN100422371C (en) | 2006-05-29 | 2006-05-29 | Chromic-nickel-free high-strength high ductility structural steel and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2006100270190A CN100422371C (en) | 2006-05-29 | 2006-05-29 | Chromic-nickel-free high-strength high ductility structural steel and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101082101A true CN101082101A (en) | 2007-12-05 |
| CN100422371C CN100422371C (en) | 2008-10-01 |
Family
ID=38911880
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2006100270190A Expired - Fee Related CN100422371C (en) | 2006-05-29 | 2006-05-29 | Chromic-nickel-free high-strength high ductility structural steel and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN100422371C (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102199699A (en) * | 2010-03-25 | 2011-09-28 | 本特勒尔汽车技术有限公司 | Method for producing a motor vehicle component, and a body component |
| CN102605190A (en) * | 2012-04-10 | 2012-07-25 | 山东远大模具材料有限公司 | Mold steel electroslag re-melting slag system and use method of mold steel electroslag re-melting slag system |
| CN103627971A (en) * | 2013-12-17 | 2014-03-12 | 西宁特殊钢股份有限公司 | Alloy structural steel for large-specification soldering tools and smelting method thereof |
| CN105568158A (en) * | 2014-10-17 | 2016-05-11 | 宝钢特钢有限公司 | Nickel-chromium-free impact-resistant bearing steel and producing method thereof |
| CN106702285A (en) * | 2016-12-12 | 2017-05-24 | 马鞍山市天马冶金材料有限公司 | Steel for fluid end of fracturing pump, and preparation process thereof |
| CN107699795A (en) * | 2017-10-26 | 2018-02-16 | 江西省中蔚建设集团有限公司 | A kind of processing method of high strength cast iron for building |
| CN109295275A (en) * | 2018-10-28 | 2019-02-01 | 石钢京诚装备技术有限公司 | A kind of 18Cr2Ni4W high alloy carburation steel and its production method |
| CN111705268A (en) * | 2020-07-01 | 2020-09-25 | 东北大学 | Steel for low-yield-ratio ultrahigh-strength high-toughness pressure-resistant shell and preparation method thereof |
| CN112593116A (en) * | 2020-12-07 | 2021-04-02 | 鹰潭盛发铜业有限公司 | Preparation method of high-strength copper-zinc alloy |
| CN114774651A (en) * | 2022-04-18 | 2022-07-22 | 营口中车型钢新材料有限公司 | Heat treatment design of YZ25SiMnMoV flat steel for railway bearing |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5421930A (en) * | 1993-11-01 | 1995-06-06 | American Telephone And Telegraph Company | Optical fiber routing method and apparatus |
| CN1039246C (en) * | 1995-05-03 | 1998-07-22 | 冶金工业部钢铁研究总院 | Low-carbon and low-alloy structural steel without chromium and nickel |
-
2006
- 2006-05-29 CN CNB2006100270190A patent/CN100422371C/en not_active Expired - Fee Related
Cited By (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US10151009B2 (en) | 2010-03-25 | 2018-12-11 | Benteler Automobiltechnik Gmbh | Method for producing a motor vehicle component, and a body component |
| CN102199699B (en) * | 2010-03-25 | 2013-12-25 | 本特勒尔汽车技术有限公司 | Method for producing motor vehicle component, and body component |
| US9057114B2 (en) | 2010-03-25 | 2015-06-16 | Benteler Automobiltechnik Gmbh | Method for producing a motor vehicle component, and a body component |
| CN102199699A (en) * | 2010-03-25 | 2011-09-28 | 本特勒尔汽车技术有限公司 | Method for producing a motor vehicle component, and a body component |
| CN102605190A (en) * | 2012-04-10 | 2012-07-25 | 山东远大模具材料有限公司 | Mold steel electroslag re-melting slag system and use method of mold steel electroslag re-melting slag system |
| CN103627971A (en) * | 2013-12-17 | 2014-03-12 | 西宁特殊钢股份有限公司 | Alloy structural steel for large-specification soldering tools and smelting method thereof |
| CN103627971B (en) * | 2013-12-17 | 2016-01-20 | 西宁特殊钢股份有限公司 | Large gauge drilling tool structural alloy steel and smelting process thereof |
| CN105568158A (en) * | 2014-10-17 | 2016-05-11 | 宝钢特钢有限公司 | Nickel-chromium-free impact-resistant bearing steel and producing method thereof |
| CN105568158B (en) * | 2014-10-17 | 2017-05-24 | 宝钢特钢有限公司 | Nickel-chromium-free impact-resistant bearing steel and producing method thereof |
| CN106702285A (en) * | 2016-12-12 | 2017-05-24 | 马鞍山市天马冶金材料有限公司 | Steel for fluid end of fracturing pump, and preparation process thereof |
| CN107699795A (en) * | 2017-10-26 | 2018-02-16 | 江西省中蔚建设集团有限公司 | A kind of processing method of high strength cast iron for building |
| CN109295275A (en) * | 2018-10-28 | 2019-02-01 | 石钢京诚装备技术有限公司 | A kind of 18Cr2Ni4W high alloy carburation steel and its production method |
| CN111705268A (en) * | 2020-07-01 | 2020-09-25 | 东北大学 | Steel for low-yield-ratio ultrahigh-strength high-toughness pressure-resistant shell and preparation method thereof |
| CN112593116A (en) * | 2020-12-07 | 2021-04-02 | 鹰潭盛发铜业有限公司 | Preparation method of high-strength copper-zinc alloy |
| CN114774651A (en) * | 2022-04-18 | 2022-07-22 | 营口中车型钢新材料有限公司 | Heat treatment design of YZ25SiMnMoV flat steel for railway bearing |
Also Published As
| Publication number | Publication date |
|---|---|
| CN100422371C (en) | 2008-10-01 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN100422371C (en) | Chromic-nickel-free high-strength high ductility structural steel and manufacturing method thereof | |
| CN105839003B (en) | A kind of 180~200mm thickness EH36 steel plates of normalizing state delivery and preparation method thereof | |
| CN101440461B (en) | Casinghead gas corrosion resistant pumping rod steel and manufacturing method thereof | |
| CN102352466B (en) | High-carbon chromium bearing steel GCr15 and production method thereof | |
| CN101775558B (en) | Fe-Cr-B cast abrasion-resistant alloy and manufacturing method thereof | |
| CN101368251B (en) | Steel plate for large-thickness hydrogen-contacting equipment and its production technology | |
| CN100507059C (en) | High-strength toughness steel for continuous sucker rod and method for manufacturing same | |
| CN109457081B (en) | Rare earth microalloyed bearing steel and preparation method thereof | |
| CN100424214C (en) | High-chromium cast steel milling ball, and its preparing method | |
| CN103114245B (en) | A kind of abrasion-proof backing block and preparation method thereof | |
| CN103540838A (en) | Steel plate for low-temperature vessel and production method thereof | |
| CN103014526A (en) | Martensitic stainless steel for valve and manufacturing method thereof | |
| CN101451219A (en) | High intensity wear-resistant steel plate and preparation method thereof | |
| CN101487102A (en) | Non-molybdenum non-nickel middle chrome wear resistant steel casting and heat treatment method thereof | |
| CN101429608A (en) | Heat-resistant alloy for exhaust valve and process for producing the same | |
| CN101691640A (en) | High strength low alloy wear resistance steel plate and preparation method thereof | |
| CN111809115B (en) | Super-thick plastic die steel with excellent impact corrosion wear resistance and preparation method thereof | |
| CN101948987A (en) | High-strength and high-toughness steel plate and manufacturing method thereof | |
| CN107130172B (en) | 400HBW grades of Brinell hardness whole constrictive type high tenacity easily weld special thick wear-resisting steel plate and its manufacturing method | |
| CN102691005A (en) | Low alloy die steel | |
| CN102605256A (en) | Rare-earth-doped bearing steel and preparation method thereof | |
| CN102383044B (en) | Multicomponent high speed steel used for preparing roller | |
| CN101649419A (en) | High-performance cold extrusion die steel and metallurgical manufacturing method thereof | |
| CN101538685B (en) | High-toughness ductile blade steel and metallurgical manufacturing method thereof | |
| CN101942606B (en) | Nitrogen alloyed austenitic hot work die steel and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| ASS | Succession or assignment of patent right |
Owner name: BAOSTEEL SPECIAL STEEL CO., LTD. Free format text: FORMER OWNER: BAOSHAN IRON + STEEL CO., LTD. Effective date: 20131210 |
|
| C41 | Transfer of patent application or patent right or utility model | ||
| COR | Change of bibliographic data |
Free format text: CORRECT: ADDRESS; FROM: 201900 BAOSHAN, SHANGHAI TO: 200940 BAOSHAN, SHANGHAI |
|
| TR01 | Transfer of patent right |
Effective date of registration: 20131210 Address after: 200940 Baoshan District aquatic Road, Shanghai, No. 1269 Patentee after: BAOSTEEL SPECIALSTEEL CO., LTD. Address before: 201900 Fujin Road, Shanghai, orchard, Baoshan District Patentee before: Baoshan Iron & Steel Co., Ltd. |
|
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20081001 Termination date: 20210529 |
|
| CF01 | Termination of patent right due to non-payment of annual fee |