CN105543713A - Micro-alloyed high-strength anti-oxidization iron-nickel alloy gas valve steel material and preparation method - Google Patents
Micro-alloyed high-strength anti-oxidization iron-nickel alloy gas valve steel material and preparation method Download PDFInfo
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Abstract
The invention relates to a micro-alloyed high-strength anti-oxidization iron-nickel alloy gas valve steel material and a preparation method. The material comprises elements such as Ni, Cr, Ti, Al, Mo, Nb, Mn, C, B, Mg, Ta, Ce, Zr, V, W, N, Fe and the like. The material can be used in a working environment with a high temperature, high load, strong oxidization and strong corrosion, is low in nickel content, has good tensile strength, good endurance strength, good fatigue strength and excellent oxidization resistance, good corrosion resistance and good resistance to fuel gas, and can be used for preparing a gas inlet valve and a gas outlet valve of a medium-high-load engine.
Description
Technical field
The invention belongs to Material Field, particularly a kind of high-strength, antioxidant iron-nickel alloy Valve Steel material of microalloying and preparation method.
Background technology
The operation that engine is vehicle provides very strong driving force, and the effect of valve is responsible for specially to input fuel and combustion gas in engine, and be the throat of engine, its importance is self-evident.The working conditions very severe of valve, mainly contain following some: the first, valve directly contacts with high-temperature fuel gas, is heated serious, and heat radiation difficulty, and therefore valve operating ambient temperature is very high, usually can reach 780-950 DEG C; The second, valve bears the effect of gas force and valve spring force, and makes to be impacted during air valve drop due to the mass force of valve actuating mechanism movement parts, and does high speed to-and-fro movement, is very easily subject to the toughness of valve material, fatigue property, wear resisting property restriction; 3rd, owing to containing mordant gas in high-temperature fuel gas, valve easily contacts with it and is corroded.This just requires need have good hot strength, antioxidant property, wear resisting property, corrosion resistance nature and fatigue property for the manufacture of the Valve Steel of valve, to adapt to its severe Working environment, and has longer work-ing life.
The usage quantity of Valve Steel is large, and over-all properties requires high.And environmental issue attention degree is deepened day by day due to people, relevant environmental regulation is constantly put into effect, higher environmental requirement and technological innovation, require that valve enterprise is by the application of novel material, novel process, new technology, improves reliability, energy saving, the environmental-protecting performance of valve product.Valve Steel at present for the manufacture of valve mainly contains three classes, comprises martensitic steel (as H15410, S65007 etc.), austenitic steel (as 21-4N and improvement steel thereof) and high-temperature alloy steel (as Inconel751, Nimonic80A etc.).The former two's hot strength, scale resistance are excellent, but need to carry out built-up welding to compensate hardness under high-temperature and wear resistance; The latter contains a large amount of nickel, not only heat-resisting but also withstand load, but cost is higher.
Develop some nickel-saving type superalloy Valve Steels at present, reduce its cost to a certain extent.But the feature of these steel shows as, cost comparatively nickel-base alloy is low, and the aspects such as its hot strength, hot hardness, wear resisting property still can not meet valve harsh operating conditions.
Because a particular job environment (high temperature, high pressure, height wash away, height corrode) of engine inlet and outlet door requires that Valve Steel material will possess good tensile strength, creep rupture strength, fatigue strength and excellent oxidation-resistance, wear resistance and resistance to combustion gas corrosion performance.In prior art, Valve Steel material mainly contains two kinds, and one is nickel base superalloy, its high comprehensive performance, but due to Ni content many (usually more than 75%), cost is high; Another kind is high temperature steel, is mainly used in moderate duty valve, and it is short that its low strength makes it easy inefficacy, life-span, though be aided with built-up welding can improve dish end face wear and corrosion behavior, easily there is built-up welding defect.
Summary of the invention
The object of this invention is to provide a kind of high-strength, antioxidant iron-nickel alloy Valve Steel material and preparation method of microalloying.Described material can use in high temperature, high loading, oxidisability is strong, corrodibility is strong Working environment, nickel content is low, there is good tensile strength, creep rupture strength, fatigue strength and excellent oxidation-resistance, wear resistance and resistance to combustion gas corrosion performance good, the inlet valve of high load engine and blast gate in can be used for preparing.
Technical scheme of the present invention is:
The high-strength, antioxidant iron-nickel alloy Valve Steel material of microalloying, the weight percentage of each component is: Ni25.0-36.0%; Cr14.0-20.0%; Ti1.9-3.0%; Al0.5-2.6%; Mo0.7-1.2%; Nb0.4-0.76%; Mn0.2-1.0%; C0.02-0.1%; B0.003-0.015%; Mg0.01-0.3%; Ta0.02-0.05%; Ce0.001-0.02%; Zr0.001-0.03%; V0.001-0.1%; W0.01-0.5%; N0.01-0.1%, surplus is Fe and impurity, and wherein the total amount of impurity is≤0.1%.
Good technical scheme is, the weight percentage of each component of material of the present invention is: Ni24.0-34.0%; Cr15.0-19.0%; Ti2.0-2.9%; Al0.7-2.5%; Mo0.7-1.14%; Nb0.44-0.76%; Mn0.23-0.88%; C0.024-0.089%; B0.005-0.013%; Mg0.04-0.17%; Ta0.025-0.044%; Ce0.005-0.016%; Zr0.006-0.027%; V0.007-0.088%; W0.03-0.45%; N0.02-0.09%, surplus is Fe and impurity.
Described impurity is Cu, Si, S, P, and its respective weight percentage is Cu≤0.01%; Si≤0.1%; S≤0.005%; P≤0.002%.
The preparation method of the high-strength, antioxidant iron-nickel alloy Valve Steel material of microalloying, has following steps:
1) electrode bar is prepared
Get above-mentioned each component according to proportioning described in claim 1 or 2, dry; Using Ni, Cr, Fe, Nb, Ta, W, C as aniseed, be warming up to aniseed under vacuum condition and melt, carry out first time refining subsequently, refining power 500kw, refining time 60min, refining Zhen in latter stage Kong Du≤3Pa; In argon gas atmosphere, add Ti, Al, Mo, B, Ce, Zr, N as small powder, be warming up to small powder and melt; Zhen Kong Du≤3Pa, carries out second time refining, refining power 500kw, refining time 40min; After refining terminates, add Mg, Mn, V, stir 5min, temperature adjustment is 1400 ~ 1600 DEG C, is cast into electrode bar;
2) esr
Be CaF by slag system proportioning (weight ratio)
2:al
2o
3:caO:MgO=65:15:15:5 electroslag slag charge fusing, step 1) described in electrode bar put remelting in slag charge into, obtain ESR ingot;
3) hammer cogging
Step 3) obtain ESR ingot 1100-1180 DEG C insulation 2-3h, open forging temperature 1000-1050 DEG C, multi-pass tempering, final forging temperature 830-960 DEG C, is swaged into square billet;
4) hot rolling
Square billet hot rolling, start rolling temperature temperature 1080-1150 DEG C, holding temperature 830-960 DEG C, finishing temperature 880-980 DEG C, rolling is circle base;
5) softening thermal treatment
Circle base holding temperature is 1050 DEG C, soaking time 1-2h, and water-cooled is to room temperature;
6) soda boiling, pickling
Round base soda boiling liquid after softening thermal treatment, at 480-550 DEG C, boils 0.5-1h; Pickle solution normal temperature pickling 20-40min;
7) cold drawing
Through step 6) soda boiling, pickling round base carry out cold drawing, drawing speed 12m/min, pass deformation is 10-15%, and total deformation is 30-60%, obtains wire and rod;
8) solid solution, ageing treatment
To obtain the high-strength, antioxidant iron-nickel alloy Valve Steel material of microalloying after the wire and rod of cold drawing carries out solid solution, ageing treatment, wherein solution treatment is: 1050-1100 DEG C of insulation 1-2h, water-cooled or oil cooling; Ageing treatment is 720-760 DEG C of insulation 12-18h.
Step 1) described aniseed is when all melting, vacuum tightness≤20Pa, refining period vacuum tightness≤3Pa.
Step 2) described remelting time, electrode bar and crystallizer packing ratio control at 0.5-0.8, and melting current is 6-10kA, and remelting voltage is 40-60V.
Step 6) mass ratio=60:40 of soda boiling liquid NaOH:NaCl, H in pickling
2sO
4: HNO
3: HF:H
2the mass ratio of O is=15:20:10:55.
In the present invention, Ni forms matrix γ phase, and forms Ni with Al, Ti etc.
3(Ti, Al) γ ˊ phase intermetallic compound, is the main strengthening phase of this alloy, is conducive to hot strength and the hot hardness of alloy.
Cr is in the design of Valve Steel, and Cr is the indispensable element improving its solidity to corrosion, oxidation-resistance.The carbide containing Cr can be separated out in ag(e)ing process, the normal temperature of material and hot strength are increased.But harmful σ phase can be formed during Cr too high levels.The scope of preferred Cr is 14.0-20.0%.
Ti and Ni forms γ ˊ phase, is conducive to hot strength and the hot hardness of alloy.There is strong bonding force between Ti and N simultaneously, by forming section TiN, crystal grain thinning.
Al and Ti is similar, can form γ ˊ strengthening phase, be conducive to hot strength and the hot hardness of alloy with Ni.This strengthening phase has higher stability and intensity within the scope of the use temperature of Valve Steel.The add-on of Ti, Al and Ti/Al produce obviously impact than by the amount of precipitation of γ ˊ phase and strengthening effect, and responsive to heat treating regime, thus need its content of Reasonable adjustment and proportioning.
Mo plays solution strengthening effect, is the substitutional atom in matrix.Mo also can form carbide, improves the hot strength of material.But during the too high levels of Mo, likely produce the embrittlement of alloy, thus the scope of preferred Mo is 0.7-1.2%.
Nb carbide, is conducive to the hot strength of material, and has obvious contribution to wear resistance.Nb and C, N combine simultaneously, the feature of can prevent grain growth during high temperature solid solution, have crystal grain thinning, improve material plasticity and hot workability.But excessive interpolation can make carbon, amount of nitrides increase, and is easy to segregation, is unfavorable for material at high temperature intensity and cold-workability.
Mn is conducive to γ phase and stablizes, favourable to the raising of intensity.But content is then unfavorable for the solidity to corrosion of material too much, and hot workability can be caused to reduce.
The excessive Cu of Cu is unfavorable for hot workability and oxidation-resistance, does not deliberately add copper in this Valve Steel Bar Wire Product, only brings into as impurity.
Si uses mainly as reductor during vacuum melting, and be also conducive to oxidation-resistance increases simultaneously.But the content of Si should strictly control, otherwise hot workability and the toughness of material can be reduced, and have σ phase to separate out, worsen material mechanical performance.
C can the deoxidation when vacuum melting, and can carbide precipitate in ag(e)ing process, and improve normal temperature and the hot strength of material, the carbide formed with W, Mo etc. also can improve material wear ability.But too high oxidation-resistance and the toughness of causing of C content reduces.
S thinks the harmful element in this material.Form sulfide with elements such as Mn, be easily enriched in crystal boundary, be unfavorable for room temperature and the high-temperature behavior of alloy.Form sulfide nonmetal inclusion simultaneously, reduce the mechanical property of materials, particularly reduce plasticity, fatigue property, also likely become crackle occurring source, cause brittle failure.Thus need strictly to control the content of S.
P is the harmful element in this material.The phosphide formed easily is separated out at crystal boundary, is unfavorable for fatigue property.The reduction of hot workability, grain-boundary strength and toughness of material can be caused simultaneously.
B can strengthen crystal boundary, is conducive to the corrosion proof improvement of intergranular.But low-alloyed initial melting temperature, will fall in the formation of low melting point boride eutectic, make hot workability worsen.
Mg is surface active element, and segregation, in the detailed annotation of crystal boundary and carbide and collective, improves interface binding power, can significantly improve alloy creep rupture life, rupture ductility and high temperature tensile properties, improve notch sensitivity and hot workability.Appropriate Mg can increase the forging property of material.
The carbide forming element that Ta is strong, formability lower than Nb higher than Ti.Ta does not change precipitated phase kind in alloy, can promote that γ ˊ phase is separated out, be conducive to hot strength.The oxidation that can slow down alloy that adds of Ta simultaneously increases, favourable to the oxidation-resistance of material.Excessive Ta is unfavorable to high temperature endurance performance.
Ce is main forms oxide compound with O, the bonding force of increase matrix and oxide film, improves oxide compound and forms.Simultaneously in vacuum metling process, the content of the detrimental impurity such as Sn, Bi can be reduced, improve ingot quality.
Zr also easily forms carbide, plays solution strengthening effect.Crystal boundary migration can be hindered, crystal grain thinning simultaneously.
V carbide, separates out tiny VC in ag(e)ing process, hinders dislocation motion.At high temperature tissue stabilization, can improve hot strength.Add-on is too high will form V
2o
5, its fusing point is lower, and zone of oxidation does not have anti-oxidation protection effect.
W and Mo is similar, and playing solution strengthening effect, is the substitutional atom in matrix.Can carbide be formed, improve hot strength.Add appropriate W to be conducive to putting forward heavy alloyed oxidation-resistance.
N can make matrix γ phase stablize, and plays solution strengthening effect.Main formation nitride, as TiN etc.TiN and alloy substrate mismatch high, ingot casting dendrite distance can be reduced, reduce macro-grain size, Laves phase and carbide size are diminished, are more evenly distributed.
Compared with prior art, beneficial effect of the present invention is:
1. with the addition of the solution strengthening such as micro Mg, Ta, Ce, Zr, V, W, N or precipitation-strengthening element, the content of detrimental impurity element S, P is controlled, in pole low-level, improve the room temperature of described material, hot strength and antioxidant property.
2., by vacuum induction melting and esr, work out that best sublimate is smelted, coagulation defect controls, the method for the duplex metallurgy of Composition Control.Easy scaling loss element al, Ti content are all controlled at zone of reasonableness, makes the difference of ESR ingot Al, Ti content end to end be less than 0.2%, ensure that ingot composition homogenizing, avoid the position that excision waits impurity more end to end, improve the yield rate of material.
3. microalloying improves the quality of Valve Steel ingot casting, and improving the hot workability of alloy, the hammer cogging temperature in 2500 tons of quick forging machines is 1100-1180 DEG C, final forging temperature 830-960 DEG C, forging warm area widened 60-100 DEG C than prior art, forging and hot rolling warm area wider; Hot rolling cogging temperature 1100-1150 DEG C, finishing temperature 880-930 DEG C, hot rolling warm area has widened 20-40 DEG C than prior art, makes material of the present invention in suitable forging range, can good plasticity and lower resistance to deformation be had to be beneficial to forging deformation by security deposit's accessory; Metal inside structure property can be improved, obtain quality forging.Because high-strength, antioxidant iron-nickel alloy Valve Steel material belongs to male sportsman, forging warm area and widening of rolling warm area are conducive to reducing resistance to deformation, ensure that metal has enough plasticity before finish-forging, enable forging obtain good structure property.In technological operation, especially showing tremendous enthusiasm time is added for minimizing, enhance productivity highly beneficial.
3. its solid solubility temperature of material of the present invention (1020-1060 DEG C), aging temp (700-750 DEG C) 30-50 DEG C lower than the solid solution of the conventional Valve Steels such as austenitic steel 21-12N, 21-4NWNb, nickel base superalloy steel Inconel751, Nimonic80A, aging temp, its room temperature, hot strength and antioxidant property are better than austenitic steel, with nickel base superalloy steel is comparable and plasticity is better.
The present invention, by adjustment precious metal nickel content and the design of microalloy unitization, improves material property, particularly hot strength and antioxidant property.Verify by experiment, the room temperature strength of described material is about 100MPa higher than comparative example, and especially 750 DEG C of hot strengths improve nearly 200MPa especially, also have a clear superiority in, in table 5 in scale resistance.
Embodiment
By proportioning described in table 1, get each component of the present invention, prepare illustrated material by the following method:
Table 1 chemical component table (wt%)
Note: comparative example is commercially available Valve Steel alloy material Ni30.
1) electrode bar is prepared
Get above-mentioned each component according to proportioning described in table 1, dry and carry out preheating in 200 DEG C of insulation 4h, dry steam.Ni, Cr, Fe, Nb, Ta, W, C are loaded furnace crucible as aniseed, vacuumizes power transmission, improve constantly with vacuum tightness, slowly promote power transmission power.After vacuum tightness is better than 20Pa, power is increased to 650kw until all aniseed all melts, and carry out first time refining subsequently, refining power 500kw, refining time 60min, refining vacuum tightness in latter stage is better than 3Pa.In argon gas atmosphere, add small powder Ti, Al, Mo, B, Ce, Zr, N after refining terminates, increased wattage makes small powder all melt to 650kw again, after vacuum tightness is better than 3Pa, carry out second time refining, refining power 500kw, refining time 40min.After refining terminates, add Mg, Mn, V, stir 5min, then sampling analysis, after composition is qualified, temperature adjustment is 1400 ~ 1600 DEG C, is cast into Φ 200 electrode bar.Sand milling finishing need be carried out in electrode bar surface, to remove descaling.Whole process not vacuum breaker, all kinds of material adds in batches, at times, to ensure good to degas, decon effect.
2) esr
By electroslag slag charge (slag system proportioning CaF
2:al
2o
3:caO:MgO=65:15:15:5) electric arc slag, carries out esr with the electrode bar prepared.Electrode bar and crystallizer packing ratio control at 0.5-0.8, and melting current controls at 6-10kA, and remelting voltage control is at 40-60V.Electroslag slag charge can desulfurization dephosphorization further, is controlled by detrimental impurity content in pole low-level, the brittle crack source that S, P content even can decrease sulfide lower than 0.005%, phosphide is formed.Additionally by slag charge refining, the optimal control of electroslag electric current, the ESR ingot of electrode bar melting speed control after esr, its end to end Al, Ti content in table 2.
3) hammer cogging
ESR ingot hammer cogging, its holding temperature controls at 1100-1180 DEG C, and soaking time controls at 2-3h, opens forging temperature 1000-1050 DEG C, final forging temperature 830-960 DEG C, and be swaged into Φ 95mm circle base, centre can multi-pass tempering.Finally be swaged into 4545mm square billet through common forging again, use for subsequent hot rolled.
4) hot rolling
Hot rolling heat holding temperature is consistent with forging holding temperature.Start rolling temperature temperature 1080-1150 DEG C finishing temperature 880-980 DEG C; Rolling specs, according to the finished product dimensional requirement, can be Φ 16,15.... until minimum Φ 8.
5) softening thermal treatment
Softening heat treated object eliminates the work hardening caused in hot rolling, drawing process, is beneficial to the distortion again of material of the present invention.Softening thermal treatment holding temperature is 1050 DEG C, and soaking time 1-2h, the type of cooling is water-cooled.
6) soda boiling, pickling
Soda boiling formula is NaOH:NaCl=60:40, soda boiling temperature 480-550 DEG C, soda boiling time 0.5-1h; Pickling formula is H
2sO
4: HNO
3: HF:H
2o=15:20:10:55, normal temperature pickling, pickling time 20-40min.
7) cold drawing
Drawing speed 12m/min, pass deformation controls at 10-15%, and total deformation controls, at 30-60%, to obtain wire and rod.Intermediate View drawing sclerotic conditions, increases once softening heat treatment step.
8) solid solution, ageing treatment
To obtain the high-strength, antioxidant iron-nickel alloy Valve Steel material of microalloying after the wire and rod of cold drawing carries out solid solution, ageing treatment, wherein solution treatment is: 1050-1100 DEG C of insulation 1-2h, water-cooled or oil cooling; Ageing treatment is 720-760 DEG C of insulation 12-18h.
9) aligning, scale blanking, polishing
Product, after service check is qualified, is aligned, scale blanking, and cut to lengthen is at 3-4m, and polishing rear surface roughness Ra is better than 2.0 μm.
Test its room temperature (table 3), high temperature tensile properties (table 4) and antioxidant property (table 5).
Table 2 ESR ingot is S, P, Al, Ti chemical component table (wt%) end to end
As shown in table 2, the present invention is by vacuum induction melting and esr duplex technique, and detrimental impurity S, P control in pole low-level, decreases the brittle crack source of sulfide, phosphide formation.In ESR ingot, easy scaling loss element al, Ti content all control at zone of reasonableness, and the difference of ESR ingot Al, Ti content is end to end minimum, and uniform composition, improves the yield rate of material.
Table 3 room temperature tensile properties, hardness balance's table
Table 3 lists GB/T23337-2009, the room-temperature mechanical property requirement to two kinds of conventional Valve Steel performances in oil engine inlet and outlet gate technique condition standard.Wherein noble metal Ni content 3.5-5.0% in 21-4NWNb material is low Ni austenite material, advantage of lower cost, and in Nimonic80A material Ni content general >=80%, be high Ni high temperature alloy, cost is relatively high, and performance is more excellent.In the embodiment of the present invention, Ni content controls at 26-34%, on the one hand controls Valve Steel cost, and the mechanical property of this example also has and is better than common austenite material, simultaneously comparable with high cost high temperature alloy again advantage on the other hand.
Table 4 high temperature tensile properties (750 DEG C)
Table 4 is 750 DEG C of high temperature tensile properties of the embodiment of the present invention.From table 3, table 4, the carbides such as Ta, Zr, V, W of adding in the embodiment of the present invention, not only play solution strengthening effect, also promote that γ ˊ phase is separated out, are conducive to room temperature and hot strength.Microalloying is very favourable to the mechanical property of material of the present invention.
Table 5 room temperature-750 DEG C of oxidation weight gains
Table 5 is the oxidation weight gain of the present embodiment under working temperature of valve condition (room temperature-750 DEG C).Rise to 750 DEG C from room temperature fast during experiment, keep constant temperature oxidation 30h, air passes into from bottom to top.This example at this temperature antioxidant property belongs to complete grade of oxidation resistance.
Compared with comparative example in table 1,3,4,5, the mechanical property of the present embodiment under room temperature and working temperature of valve condition is all more excellent, the microalloying of Mg, Ta, Zr, V, elements such as w is especially beneficial to the high-temperature behavior of material, the oxidation that can slow down alloy that adds of the addition of C r, Ta, W increases, favourable to the oxidation-resistance of material.
Claims (7)
1. a high-strength, antioxidant iron-nickel alloy Valve Steel material for microalloying, it is characterized in that, the weight percentage of each component is: Ni25.0-36.0%; Cr14.0-20.0%; Ti1.9-3.0%; Al0.5-2.6%; Mo0.7-1.2%; Nb0.4-0.76%; Mn0.2-1.0%; C0.02-0.1%; B0.003-0.015%; Mg0.01-0.3%; Ta0.02-0.05%; Ce0.001-0.02%; Zr0.001-0.03%; V0.001-0.1%; W0.01-0.5%; N0.01-0.1%, surplus is Fe and impurity.
2. material according to claim 1, is characterized in that: the weight percentage of described each component is: Ni24.0-34.0%; Cr15.0-19.0%; Ti2.0-2.9%; Al0.7-2.5%; Mo0.7-1.14%; Nb0.44-0.76%; Mn0.23-0.88%; C0.024-0.089%; B0.005-0.013%; Mg0.04-0.17%; Ta0.025-0.044%; Ce0.005-0.016%; Zr0.006-0.027%; V0.007-0.088%; W0.03-0.45%; N0.02-0.09%, surplus is Fe and impurity, and wherein the total amount of impurity is≤0.1%.
3. material according to claim 1 and 2, is characterized in that: described impurity is Cu, Si, S, P, and its respective weight percentage is Cu≤0.01%; Si≤0.1%; S≤0.005%; P≤0.002%.
4. the preparation method of the high-strength, antioxidant iron-nickel alloy Valve Steel material of microalloying, is characterized in that there are following steps:
1) electrode bar is prepared
Get above-mentioned each component according to proportioning described in claim 1 or 2, dry; Using Ni, Cr, Fe, Nb, Ta, W, C as aniseed, be warming up to aniseed under vacuum condition and melt, carry out first time refining subsequently, refining power 500kw, refining time 60min, refining Zhen in latter stage Kong Du≤3Pa; In argon gas atmosphere, add Ti, Al, Mo, B, Ce, Zr, N as small powder, be warming up to small powder and melt; Zhen Kong Du≤3Pa, carries out second time refining, refining power 500kw, refining time 40min; After refining terminates, add Mg, Mn, V, stir 5min, temperature adjustment is 1400 ~ 1600 DEG C, is cast into electrode bar;
2) esr
Be CaF by the weight ratio of slag system proportioning
2: Al
2o
3: CaO:MgO=65:15:15:5 electroslag slag charge fusing, step 1) described in electrode bar put remelting in slag charge into, obtain ESR ingot;
3) hammer cogging
Step 3) obtain ESR ingot 1100-1180 DEG C insulation 2-3h, open forging temperature 1000-1050 DEG C, multi-pass tempering, final forging temperature 830-960 DEG C, is swaged into square billet;
4) hot rolling
Square billet hot rolling, start rolling temperature temperature 1080-1150 DEG C, holding temperature 830-960 DEG C, finishing temperature 880-980 DEG C, rolling is circle base;
5) softening thermal treatment
Circle base holding temperature is 1050 DEG C, soaking time 1-2h, and water-cooled is to room temperature;
6) soda boiling, pickling
Round base soda boiling liquid after softening thermal treatment, at 480-550 DEG C, boils 0.5-1h; Pickle solution normal temperature pickling 20-40min;
7) cold drawing
Through step 6) soda boiling, pickling round base drawing, drawing speed 12m/min, pass deformation is 10-15%, and total deformation is 30-60%;
8) solid solution, ageing treatment
To obtain the high-strength, antioxidant iron-nickel alloy Valve Steel material of microalloying after the wire and rod of cold drawing carries out solid solution, ageing treatment, wherein solution treatment is: 1050-1100 DEG C of insulation 1-2h, water-cooled or oil cooling; Ageing treatment is 720-760 DEG C of insulation 12-18h.
5. method according to claim 4, is characterized in that: step 1) described aniseed is when all melting, vacuum tightness≤20Pa, refining period vacuum tightness≤3Pa.
6. method according to claim 4, is characterized in that: step 2) described remelting time, electrode bar and crystallizer packing ratio control at 0.5-0.8, and melting current is 6-10kA, and remelting voltage is 40-60V.
7. method according to claim 4, is characterized in that: step 6) mass ratio=60:40 of soda boiling liquid NaOH:NaCl, H in pickling
2sO
4: HNO
3: HF:H
2the mass ratio of O is=15:20:10:55.
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