CN102634740A - High-plasticity economical duplex stainless steel and manufacturing method thereof - Google Patents
High-plasticity economical duplex stainless steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention relates to a high-plasticity economical duplex stainless steel and a manufacturing method thereof. The high-plasticity economical duplex stainless steel comprises the following chemical components by weight part: 0.01-0.06% of C, 0.1-1.0% of Si, 0.5-4.0% of Mn, 19.5-22.0% of Cr, 1.8-3.5% of Ni, 0.1-0.18% of N, 0.5-1.3% of Mo, 0.1-1.0% of Cu and the balance of Fe and inevitable impurities. According to the invention, Ni is replaced by Mn and N, so that the cost is lowered; the contents of Cr and Mo are adjusted, so that the steel has excellent corrosion resistance, higher plasticity, excellent low-temperature toughness, and excellent welding property; the Md 30/50 is controlled at 50-100 DEG C; and PREN value is 23-29. Thus, the high-plasticity economical duplex stainless steel can be widely applied to an environment with higher demand on corrosion resistance and plasticity, such as heat exchanger, water tank, and the like, so that the 304 austenitic stainless steel containing 8% of nickel and the 316 stainless steel containing of 10% Ni and 2% of Mo are replaced under the conditions of room temperature and low temperature.
Description
Technical field
The present invention relates to duplex stainless steel and method of manufacture thereof, especially a kind of economical diphase stainless steel of high-ductility and method of manufacture thereof.
Background technology
Form by ferritic and austenite two-phase under the duplex stainless steel room temperature, and the existence of two-phase structure makes duplex stainless steel have the advantage of ferritic stainless steel and austenitic stainless steel concurrently.Compare with austenitic stainless steel, the intensity of duplex stainless steel, particularly ys significantly improves, and approximately is the twice of austenitic stainless steel; Intergranular corrosion resistance, anticorrosion stress-resistant, resistance to corrosion fatigue and wear resisting property significantly improve.With the ferritic stainless steel ratio, its toughness is high, brittle transition temperature is low, intergranular corrosion resistance and weldableness are significantly improved, and has kept the advantage that the ferritic steel thermal conductivity is high, the coefficient of expansion is little simultaneously.
Three important stages have been experienced in the development of duplex stainless steel up to now.The trade mark of being developed before 1971 is a first-generation duplex stainless steel, because the restriction of smelting condition, the content of C, N all can't accurately be controlled, and its welding back performance sharply descends.The trade mark of exploitation in 1971～1989 years belongs to s-generation duplex stainless steel, and representing steel grade is S32205.Invention and application by means of nineteen sixty-eight stainless steel precision sweetening process-argon oxygen decarburization (AOD); Can make that nitrogen content significantly improves in the duplex stainless steel; Carbon content is accurately controlled; Thereby significantly improve the toughness and the corrosion resistance nature of weld seam, heat affected zone, nitrogen has also reduced the formation speed of phase between poisonous metal simultaneously.Development of technology makes dual phase steel be able to be widely used in a plurality of fields such as offshore oil platform, chemical industry, papermaking.The trade mark that occurs after nineteen ninety is a third generation duplex stainless steel, and its development presents 2 kinds of trend.Further improve steel interalloy constituent content on the one hand to obtain more HS and superior corrosion resistance ability more, like the SAF2906 and the SAF3207 of Sweden SANDVIK exploitation.Develop low nickel content on the other hand and do not contain Mo or only contain the economical diphase stainless steel of a small amount of Mo, to reduce cost, like LDX2101 etc.
Along with the importance to manufacturers and user of precious metal resource highlights gradually, the exploitation of economical diphase stainless steel becomes the important R&D direction of current duplex stainless steel.Economical diphase stainless steel is through special alloy designs, reduces the content of precious metal nickel and molybdenum in the alloy, thereby significantly reduces material cost.Austenite equivalent calculation formula commonly used is suc as formula shown in (1):
Ni
eq＝Ni+30(C+N)+0.5Mn+0.25Cu (1)
The PREN (equivalent of anti-the spot corrosion) that estimates the anti-pitting attack performance of duplex stainless steel is shown in formula (2):
PREN (equivalent of anti-the spot corrosion)=Cr%+3.3Mo%+30N%-Mn% (2)
Can be known by formula (1), can adopt Mn, N, Cu to replace Ni, thereby reduce cost, replace traditional high molybdenum, the duplex stainless steel of high nickel content, this is the basis of economical diphase stainless steel exploitation.
N is one of most important alloying element in the duplex stainless steel, and is with low cost, is very strong austenite former.Can know that by formula (1) it has formed austenitic ability is 30 times of Ni.Simultaneously can know that by formula (2) N can significantly improve the PREN value of material, thereby help improving the solidity to corrosion of duplex stainless steel steel.In addition, N also is the key element that guarantees the duplex stainless steel welding property.Smelt the difficulty increase but the raising of N content can cause, hot workability descends.
Mn is an alloying element cheaply, but Mn has disadvantageous effect to the duplex stainless steel corrosion resistance nature, and shown in formula (2), the manganese of promptly every interpolation 1% will make alloy PREN value reduce by 1.If guarantee the superior corrosion resistance ability of material, must its content of control.The reason that Mn influences pitting corrosion resistance is that manganese and sulphur form MnS, or along with manganese amount in the steel increases, the chrome content among the MnS reduces, and caused MnS is mixed in the dissolving in the corrosive medium, usually becomes the starting point of spot corrosion, crevice corrosion.
Cu also is an austenite former, but the austenite formation ability of Cu has only 1/4 of nickel.A very important effect of Cu is a stable austenite, reduces the work hardening tendency, thereby improves stainless plasticity.But the Cu too high levels can cause hot workability to descend in the duplex stainless steel.
To third generation duplex stainless steel, comprising existing economical diphase stainless steel from the first-generation, all is high alloy composition system.The alloy content height causes in the duplex stainless steel austenitic stability very high.From high temperature cooling to cryogenic process martensitic transformation taking place, and in deformation process, does not almost have martensite to produce yet.With M
sWith Md
30/50Estimate austenitic stability, its classical expression formula is suc as formula shown in (3) and the formula (4).M
sBe the beginning temperature spot of austenite in the process of cooling to martensitic transformation, and Md
30/50Characterize austenitic stability in the deformation process.This temperature is high more, is illustrated in to be out of shape under the higher temperature austenite to take place to martensitic transformation.
M
s＝1305-61.6Ni％-41.7Cr％-33.3Mn％-27.8Si％-1667(C+N)％ (3)
Md
30/50＝580-520C％-2Si％-16Mn％-16Cr％-23Ni％-300N％-26Cu％-10Mo％..(4)
The M of all duplex stainless steels
sPoint is all very low, gathers M if consider alloying element C, N partially in that Ovshinsky is intravital
sPoint is lower.Therefore duplex stainless steel does not form martensite from the process of high temperature cooling to room temperature.And the Md of all up to now duplex stainless steels
30/50Therefore temperature spot, produces or only produces the martensite of trace hardly all below 40 in the deformation at room temperature process.
When the alloy content in the duplex stainless steel reduces, Md
30/50To rise.If the adjustment of passing through alloying constituent is with Md
30/50Temperature is controlled at suitable scope, and the austenite in the deformation process in the duplex stainless steel will be to martensitic transformation, thereby TRIP (phase-change induced plastic) effect takes place, significantly the plasticity of duplex stainless steel.On the contrary, if Md
30/50Too high or too low, unfavorable to the plasticity of duplex stainless steel on the contrary.Though the TRIP effect is a kind of mechanism of raising alloy plasticity commonly used, in existing economical diphase stainless steel patent, does not all relate to.
Chinese patent CN101215674 is typically with Mn, the N economical diphase stainless steel for Ni.Its Mn content does not contain Ni up to being 4-7%.Consider that its Cr content is 18-20%, and do not contain Mo, the PREN value of this duplex stainless steel is lower, is unfavorable for the corrosion resisting property of material.
European patent EP 1327008 has been announced a kind of austenite-ferrite duplex stainless steel, and its composition range (weight %): 0.02～0.07%C, 3.0～8.0%Mn, 19.0～23.0%Cr, 1.1～1.7%Ni, 0.1～2.0%Si, 0.15～0.3%N, the alloying element that possibly comprise have and be not more than 1.0% Mo or W, be not more than 1.0% Cu.The N content of steel grade is controlled at about 0.2%, has guaranteed the new ability of good welding, and the application of having achieved success in fields such as bridge, storage tank, nuclear powers at present becomes the representative steel grade of economical diphase stainless steel.But the Ni element in the steel is lower, has reduced low-temperature impact toughness; Mn content is higher, so its solidity to corrosion can only reach 304 level.
For further improving the low-temperature flexibility of economical diphase stainless steel, Chinese patent CN101613839 has announced a kind of austenite-ferrite duplex stainless steel of excellent in low temperature toughness.The key of this patent is for improving low-temperature flexibility, being increased to Ni content to 1.8～4.0%; For keeping suitable pitting resistance, reduce below the Mn content to 1.5% simultaneously.
The economical diphase stainless steel that European patent EP 2258885 is designed is controlled at 2-4% with Mn content, thereby has improved the corrosion resistance nature of material.The key point of this patent is to have added a certain amount of V, utilizes V to suppress the activity of N, thereby avoids in the weld heat-affected zone nitride of Cr to separate out, thereby improves the erosion resistance and the impelling strength of weld seam.
For further improving the corrosion resistance nature of material, U.S. Pat 479863 is controlled at Mn content below 4%, improves Cr content simultaneously to 21-24.5%, and adds a spot of Mo (＜1%).Through controlling the content of these and the closely-related alloying element of material corrosion resistance, its corrosion resistance nature can reach the level of austenitic stainless steel 316L.
Equally, for further improving the corrosion resistance nature of material, Chinese patent CN101090988 is increased to 0.5～2.5% with Mo.The compositing range of the alloy compositions of its patented claim guarantees that alloy CPT is higher than 20 ℃, and its corrosion resisting property is superior to SUS304 steel and 316L steel.
More than the patent of all economical diphase stainless steels all do not relate to the plasticity that improves material.
Summary of the invention
The object of the invention is to provide a kind of economical diphase stainless steel and method of manufacture thereof of high-ductility; With the corrosion resistance nature of excellence and higher plasticity; Can be applied to field that material plasticity and solidity to corrosion are had higher requirements, like fields such as heat exchanger, water tanks.
For realizing above-mentioned purpose, technical scheme of the present invention is:
Thereby stainless steel of the present invention replaces Ni with Mn, N to reduce cost, thereby under room temperature and coldcondition, replaces 316 stainless steels that contain 304 austenitic stainless steels of 8% nickel and contain 10%Ni, 2%Mo.Simultaneously, for guaranteeing higher plasticity, add a spot of Cu, emphasis is with the Md of formula (4) definition
30/50To be controlled at 50～100 ℃; For guaranteeing excellent corrosion resistance nature, Mn content is controlled at 0.5～4.0%, Cr content is controlled at 19.5～22.0%, Mo content is controlled at 0.5-1.3%, with the PREN value that guarantees (2) definition by formula 23～29.
Particularly, the economical diphase stainless steel of a kind of high-ductility of the present invention, its chemical component weight per-cent is: C0.01～0.06%; Si0.1～1.0%, Mn0.5～4.0%, Cr19.5～22.0%; Ni1.8～3.5%, N0.1～0.18%, Mo0.5～1.3%; Cu0.1～1.0%, all the other are Fe and unavoidable impurities.
Again, the economical diphase stainless steel of high-ductility of the present invention also comprises W and/or B, W≤0.5%, B≤0.01%, weight percent meter.
In the composition design of economical diphase stainless steel of the present invention:
Carbon carbon is strong austenite former, can know from formula (1), and its austenite formation effect is equivalent to 30 times of Ni, therefore can replace Ni to a certain extent, promotes the formation of austenite structure.In addition, can know that carbon is very strong austenite stable element, can suppress austenitic phase transformation from formula (3), (4).But when carbon content was too high, carbon combined the back to form rich chromium carbide at crystal boundary with chromium, cause intergranular corrosion.Especially in welding process, carbide is separated out rapidly, will cause the corrosion resistance nature of welding zone and mechanical property significantly to descend.Cross low carbon content and will increase difficulty and cost in the preparation process.Therefore, the design carbon content is 0.01～0.06% in the steel of the present invention.
Silicon silicon is the element that contains usually in the iron and steel, because silicon is to be good deoxidant element in the fusion process, contains the silicon more than 0.1% in the therefore general dual phase steel.In duplex stainless steel, silicon is that ferritic forms and stable element, and the nickel equivalent that the too high meeting of silicone content causes being complementary with it improves, and increases cost.The more important thing is that silicon can quicken separating out of intermetallic phase, unfavorable for manufacturing and use.Therefore, design of Si content is 0.1～1.0% in the steel of the present invention.
Manganese is that a kind of more weak relatively austenite forms and stable element, can utilize manganese to replace nickel to a certain extent, and the interpolation of manganese can significantly improve the solubleness of nitrogen in addition, so economical diphase stainless steel contains higher Mn usually.But manganese all is negative to the influence of stainless erosion resistance basically.According to the experimental formula (2) of the anti-pitting attack performance of stainless steel, the manganese of every interpolation 1% will make alloy PREN value reduce by 1, be equivalent to offset the Cr that adds 0.3% Mo or 1% raising to pitting resistance.For taking into account the corrosion resistance nature of material, emphasis control Mn content is 0.5%～＜4.0% in the steel of the present invention.
Chromium chromium is the most important element that stainless steel obtains corrosion resistance nature, also is a kind of ferrite former, but the while stable austenite, so Cr is a most important alloying element in the duplex stainless steel.As far as duplex stainless steel, when chromium content is low, solidity to corrosion will descend, and martensitic phase might appear in the while, and is all unfavorable to mechanics and corrosion resistance nature, so Cr content of the present invention is minimum is controlled to be 19.5%.But when the chromium too high levels, not only can increase the tendency of separating out of intermetallic phase, carbide and nitride, and, can increase austenite former content, thereby increase cost and make austenite be difficult to take place martensitic transformation for obtaining duplex structure.Therefore Cr content is the highest in the steel of the present invention is controlled at 22.0%.
Nitrogen nitrogen element is an important element indispensable in the modern duplex stainless steel.At first N is a kind of formation and stable austenite element mutually.In austenite equivalent calculation formula (1), the austenite formation ability of nitrogen is 30 times of nickel.According to formula (3) and formula (4), nitrogen also is a kind of very strong austenite stable element.In addition, nitrogen can improve the corrosion resistance nature of austenite phase, especially anti-pitting attack performance and slit and corrosion resistant performance, and in the calculation formula (2) of PREN value, its equivalent of anti-the spot corrosion is 30 times of chromium.When but nitrogen content is too high,, reduce the toughness and the solidity to corrosion of material with increasing the risk that nitride forms.High nitrogen content can improve melting and hot worked difficulty simultaneously, causes being difficult to producing existing producing on the line.Therefore, nitrogen in steel content of the present invention is controlled at 0.1～0.18%.
The molybdenum molybdenum is very beneficial for improving the corrosion resistance nature of steel, especially with the situation of chromium compound action under.According to RREN value calculation formula (2), its equivalent of anti-the spot corrosion is 3.3 times of chromium.Its mechanism is to stablize passive film and promote the enrichment of chromium element in passive film.Corrosion resistance nature for guaranteeing that material is excellent is controlled at Mo content more than 0.5%.But the molybdenum too high levels will cause between friable metal the acceleration of phase to be separated out, and increase cost of alloy simultaneously, so the molybdenum content in the steel of the present invention be controlled at below 1.3%.
Copper copper is a kind of more weak austenite former, can substitute part of nickel.The adding of copper can improve the erosion resistance of dual phase steel in reductive acid, helps improving the slit and corrosion resistant performance simultaneously.What is more important, Cu is the alloying element of stable austenite, can reduce austenitic cold hardening speed, thereby improves the plasticity of material; In addition, Cu also can improve the plasticity of ferritic structure to a certain extent.Therefore, must add a certain amount of Cu among the present invention.But be unfavorable for hot workability during the copper too high levels.Therefore Cu content is controlled at below 1.0% in the steel of the present invention.
Tungsten tungsten is one of optional element among the present invention.The effect of tungsten in dual phase steel is similar with molybdenum, can improve the corrosion resistance nature of steel.Tungsten can also reduce the activity at austenite/ferritic phase interface, suppresses the formation of intermetallic phase.Promote intermetallic phase to generate when but W content is too high on the contrary.Therefore W content is controlled at below 1.0% in the steel of the present invention.
Boron boron also is one of optional element of the present invention.The adding of boron mainly is for improving the hot workability of duplex stainless steel.But the B too high levels can cause forming in the duplex stainless steel compound of B, seriously reduces the plasticity and the toughness of material.Therefore B content is controlled at below 0.02% among the present invention.
The method of manufacture of the economical diphase stainless steel of a kind of high-ductility of the present invention, the method for manufacture of this duplex stainless steel may further comprise the steps:
1) smelts
The stainless steel weight percent is: C0.01～0.06%, and Si0.1～1.0%, Mn0.5～4.0%, Cr19.5～22.0%, Ni1.8～3.5%, N0.1～0.18%, Mo0.5～1.3%, Cu0.1～1.0%, all the other are Fe and unavoidable impurities; Smelt and adopt vacuum induction to smelt, electric furnace-argon oxygen decarburization AOD or electric furnace-argon oxygen decarburization AOD-external refining LF stove is smelted;
2) molten steel is carried out die casting or continuous casting, the control superheating temperature is 20～50 ℃ during die casting, and the slab pulling rate is 0.8～2m/min;
3) die casting base or continuous casting steel billet are put into process furnace and are heated to 1100～1250 ℃ and insulation after, on forging line or hot rolling unit, be machined to the required specification of 3～20mm, anneal then or annealing and pickling, its annealing temperature is controlled at 1030～1130 ℃;
4) hot rolled coil after the hot-roll annealing or hot-rolled sheet are machined to 0.1～3mm at cold rolling unit, carry out annealing and pickling or clean annealing then, annealing temperature is controlled at 1030～1130 ℃;
5) annealing, 200～450 ℃ of annealing temperatures are in the cold working process; Material can produce certain strain-induced martensite; For guaranteeing the performance of material after processing, at 200-450 ℃ it is carried out martensite and reverse change annealing, thereby eliminate the martensite that produces in the cold working process.
The present invention compared with prior art has the following advantages and positively effect:
(1) utilizes the Mn of 0.5-4.0% and the N of 0.1-0.18% to substitute Ni, Ni content is controlled at 1.8～3.5%, both guaranteed impelling strength under the low temperature of alloy, significantly reduce the material cost of alloy again;
(2) Mn content is controlled to 0.5～4.0%, reduce the disadvantageous effect of manganese effectively corrosion resistance nature; Cr content is controlled at 19.5～22.0%; And Mo content is increased to more than 0.5%, nitrogen content is controlled at 0.1～0.18%, guarantee that PREN value by formula (2) definition is between 23～29; Thereby guarantee that material has excellent corrosion resistance nature, especially anti-spot corrosion and stress corrosion performance;
(3) add a spot of Cu, improve the plasticity of material, emphasis is that the total amount of alloying element is controlled, the Md of feasible by formula (4) definition
30/50At 50～100 ℃, thereby utilize the austenite transformation of martensitic phase in opposite directions, produce the existing higher plasticity of economical diphase stainless steel.
(3) duplex stainless steel of the present invention existing stainless steel capable of using produces the line batch process; Concrete preparation method is casting after vacuum induction furnace, electric furnace-AOD stove smelting or electric furnace-AOD-LF stove are smelted, and the control superheating temperature is about 20～50 ℃ when die casting, and cooperates quick cooling; Or adopt cooling rate continuous cast method faster; Avoid the effusion of nitrogen, the control superheating temperature is 20～50 ℃ during continuous casting, and the slab pulling rate is 0.8～2m/min.Because of material has thermoplasticity and cold-forming property preferably, can carry out the production of hot rolling and cold rolling coil, plate etc.Hot rolling and cold rolling annealing temperature are controlled between 1030～1150 degree.
(4) alloy has good anti-pitting attack performance and plasticity.The unit elongation δ of cold rolled sheet is 40～55%; Pitting attack current potential (GB/T17899-1999) is 400～800mv.
Description of drawings
Fig. 1 is embodiments of the invention 1 alloy metallographic structures.
Fig. 2 carries out the variation of martensite content in the tensile deformation process for embodiments of the invention 2 alloys.
Embodiment
Below in conjunction with embodiment the present invention is further specified.
The embodiment of the invention is an example with the Production Flow Chart of electric furnace-AOD-continuous casting and hot rolling-annealing and pickling-cold rolling-annealing and pickling:
Ferrochrome, ferronickel and steel scrap etc. are added electric furnace, melt, pour molten steel into the AOD stove subsequently with molten iron; In the AOD stove, take off C, take off O, take off S and increase N, control the blowing of N; When the smelting composition reaches requirement, pour molten steel into tundish, and on vertical-bending caster, cast.The superheating temperature of continuous casting is 20～50 ℃, and the slab pulling rate is 0.8～2m/min.Continuous casting steel billet is put into process furnace be heated to 1100～1250 ℃, after being rolled down to desired thickness on the hot continuous rolling unit, batch.Carry out the continuous annealing pickling then, annealing temperature is controlled at 1030-1150 ℃, thereby acquisition is near the tissue and the non-scale surface of 1: 1 ferritic-austenitic double structure.It is thick at last the coil of strip after the hot-roll annealing to be cold-rolled to 1mm, anneals and pickling, to obtain high-quality surface and ideal tissue again.Annealing temperature is 1030～1150 ℃.
Table 1 is depicted as the chemical ingredients of embodiment of the invention alloy; Table 1 has provided the economical diphase stainless steel S32101, the S32304 that have developed at present of example as a comparison simultaneously, and the chemical ingredients of hoping to carry out in certain fields with steel grade of the present invention alternate 304 (S30400), 316 (S31600) austenitic stainless steel.Its intensity, unit elongation record according to GB/T228-2007, and pitting potential records according to GB/T17899-1999.
The metallographic structure of the alloy of embodiment 1 is as shown in Figure 1.With carrying out electrolytic corrosion after sample polishing and the polishing, etching reagent is 40Gkoh+100mlH
2O, corrosion current 0.3～0.8A/cm
2, under metaloscope, the austenite ratio is analyzed at last through the quantitative metallography method.Black is organized as ferritic among the figure, and white is organized as austenite, and austenite accounts for 48% mutually.
The variation of martensite content is as shown in Figure 2 in organizing in embodiment 2 drawing process.Tension specimen is pressed the JIS-13B standard manufacture; After being stretched to the predetermined deformation amount on the MTS-810 drawing machine, promptly stop and unloading; The variation of magnetic before and after measure stretching through the magnetic appearance is then confirmed whether produce martensite in the drawing process and is roughly confirmed what of martensite content with this.Fig. 2 explanation is in the process of tensile deformation, and the part austenite undergoes phase transition, and has generated strain-induced martensite, and this is the key reason that causes its plasticity to improve.
Visible by table 1, table 2, steel of the present invention is owing to utilize the Mn of 0.5-4.0% and the N of 0.1-0.18% to substitute Ni, reaches 8% 304 austenitic stainless steels and contains Ni and reach 10% and contain Mo and reach 2% 316 austenitic stainless steels than containing Ni, and is more economical.Because control Mn content is in suitable level, and improved alloying element contents such as Cr, Mo, alloy has obtained excellent corrosion resistance nature, and pitting potential is significantly higher than 304 austenitic stainless steels, near in addition surpass 316 austenitic stainless steels; Owing to added a certain amount of Cu, and adjusted the total amount of alloying elements such as Ni, N, Mn, Cr, with the Md of material
30/50Point control between 50～100 ℃, thereby make material production phase-change induced plastic effect, significantly improved the plasticity of material, its thin plate unit elongation is compared with respect to S32101, S32304 duplex stainless steel, improves about more than 30%.
Table 1 unit: weight percent
Table 2
Claims (4)
1. the economical diphase stainless steel of a high-ductility, its chemical component weight per-cent is: C0.01～0.06%, Si0.1～1.0%; Mn0.5～4.0%, Cr19.5～22.0%, Ni1.8～3.5%; N0.1～0.2%; Mo0.5～1.3%, Cu0.1～1.0%, all the other are Fe and unavoidable impurities.
2. the economical diphase stainless steel of high-ductility as claimed in claim 1 is characterized in that, also comprises W and/or B, W≤0.5%, B≤0.01%, weight percent meter.
3. the method for manufacture of the economical diphase stainless steel of a high-ductility may further comprise the steps:
1) smelts
The stainless steel weight percent is: C0.01～0.06%, and Si0.1～1.0%, Mn0.5～4.0%, Cr19.5～22.0%, Ni1.8～3.5%, N0.1～0.18%, Mo0.5～1.3%, Cu0.1～1.0%, all the other are Fe and unavoidable impurities; Smelt and adopt vacuum induction to smelt, electric furnace-argon oxygen decarburization AOD or electric furnace-argon oxygen decarburization AOD-external refining LF stove is smelted;
2) molten steel is carried out die casting or continuous casting, the control superheating temperature is 20～50 ℃, and the slab pulling rate is 0.8～2m/min;
3) die casting base or continuous casting steel billet are put into process furnace and are heated to 1100～1250 ℃ and insulation after, on forging line or hot rolling unit, be machined to 3～20mm, anneal then or annealing and pickling, its annealing temperature is controlled at 1030～1130 ℃;
4) hot rolled coil, hot-rolled sheet after the hot-roll annealing are machined to 0.1～3mm at cold rolling unit, carry out annealing and pickling or clean annealing then, annealing temperature is controlled at 1030～1130 ℃;
5) annealing, 200～450 ℃ of annealing temperatures are carried out martensite and are reversed change annealing, thereby eliminate the martensite that produces in the cold working process.
4. the method for manufacture of the economical diphase stainless steel of high-ductility as claimed in claim 3 is characterized in that, said rust steel also comprises W and/or B, W≤0.5%, B≤0.01%, weight percent meter.
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| US10501820B2 (en) | 2015-02-17 | 2019-12-10 | Sandvik Materials Technology Deutschland Gmbh | Method for producing a strand from stainless steel and strand made of stainless steel |
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| CN105886956B (en) * | 2016-07-01 | 2017-10-31 | 东北大学 | A kind of economizing type two-phase stainless steel sheet and preparation method thereof |
| CN105886956A (en) * | 2016-07-01 | 2016-08-24 | 东北大学 | Economical duplex stainless steel sheet and preparation method thereof |
| CN107779788A (en) * | 2017-10-31 | 2018-03-09 | 福州大学 | A kind of two phase stainless steel and its solid solution treatment process |
| CN110487826A (en) * | 2019-08-06 | 2019-11-22 | 燕山大学 | The test method of deformation inductdion ε martensite transfor mation content |
| CN110487826B (en) * | 2019-08-06 | 2020-06-12 | 燕山大学 | Method for testing transformation content of deformation induced epsilon martensite |
| CN113025891A (en) * | 2021-02-08 | 2021-06-25 | 江阴兴澄特种钢铁有限公司 | Duplex stainless steel S32101 steel plate and manufacturing method thereof |
| CN113025891B (en) * | 2021-02-08 | 2022-07-22 | 江阴兴澄特种钢铁有限公司 | Duplex stainless steel S32101 steel plate and manufacturing method thereof |
| CN115466902A (en) * | 2022-06-30 | 2022-12-13 | 福建青拓特钢技术研究有限公司 | Niobium-containing economical high-plasticity duplex stainless steel with excellent intergranular corrosion resistance and manufacturing method thereof |
| CN115287521A (en) * | 2022-07-20 | 2022-11-04 | 山西太钢不锈钢股份有限公司 | Method for improving low-temperature impact toughness of economical duplex stainless steel medium plate for nuclear power |
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