CN106929710A - Ultra-supercritical steam turbine rotor high-strength and high ductility heat-resisting alloy and preparation method thereof - Google Patents
Ultra-supercritical steam turbine rotor high-strength and high ductility heat-resisting alloy and preparation method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
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Abstract
A kind of ultra-supercritical steam turbine rotor high-strength and high ductility heat-resisting alloy and preparation method thereof, belongs to heat-resisting alloy technical field.Alloying component contains by mass percentage：C：0.02~0.04%, Cr：19.0~20.5%, Mo:6.0~8.1%, Co:9.0~12.0%, W：0.10~0.50%, Al：1.40~1.60%, Ti：1.55~1.95%, Nb：0.10~0.60%, Mg：0.002~0.015%, Zr：0.002~0.01%, B：0.002~0.008%, Si：No more than 0.10%, Mn：No more than 0.20%, S：No more than 0.002%, P：No more than 0.004%, balance of Ni.And Al+Ti mass percents meet：3.0%≤Al+Ti≤3.5%, Ti/Al mass percents meet 0.95≤Ti/Al≤1.20.Advantage is that the heat-resisting alloy that can make acquisition particular organization has the characteristic of high-strength and high ductility, it is adaptable to which the high temperature large component such as 700 DEG C~760 DEG C steam parameter extra-supercritical unit turbine rotors is used.
Description
Technical field
The invention belongs to heat-resisting alloy technical field, a kind of more particularly to ultra-supercritical steam turbine rotor high-strength and high ductility
Heat-resisting alloy and preparation method thereof, it is adaptable to which 700 DEG C~760 DEG C steam parameter ultra supercritical coal-fired unit turbine rotors are contour
Warm large component is used.
Background technology
With the development of society, demand more and more higher of the human society to electric power.For China, thermal power output is accounted for
The 80% of national gross generation.It is expected that in a very long time thermal power generation from now on will be China or even global topmost hair
Electrically.It is to improve the vapor (steam) temperature and pressure of unit to improve the maximally effective approach of the thermal efficiency.Grinding at first current countries in the world
The 700 DEG C of steam parameter ultra supercritical power stations entered, its generating thermal efficiency is estimated up to more than 50%.American-European, the day from the beginning of this century
This and South Korea all carry out 700 DEG C of steam parameter ultra supercritical power station R＆D works in succession.2010, National Energy Board was in the people
The great hall is announced to set up " national 700 DEG C of ultra-supercritical power generation technology Innovation Alliances ", indicates that China formally carries out 700 DEG C
Ultra supercritical coal-fired unit technology national development plan.
With the rising of vapor (steam) temperature and pressure, ultra supercritical unit proposes higher to relative keys heat proof material
Use requirement.Generally under arms under operating mode, material should meet：(1) 10 under service temperature5After hour, creep rupture strength is not less than
100MPa；(2) under arms in 2 × 105Material oxidation corrosion layer thickness after h is less than 2mm；(3) service temperature (700 DEG C~
760 DEG C) under it is long when structure stability；(4) intensity higher, toughness and fatigue strength；(5) excellent castability, be processed into
Shape and weldability.For above-mentioned harsher performance requirement, traditional ferrite and austenitic heat-resistance steel can not meet
Use requirement, the high temperature section part of generating set must select Refractoloy.
The Refractoloy of exploitation is mainly divided to two classes at present：One class is solution strengthening type alloy, and another kind of is strong timeliness
Change type alloy.For the more complicated large high-temperature part of operating mode, the material of leading candidate with when acting type alloy based on, such as Japan east
Sesame company is based on the alloy TOS1X-2 of proprietary alloy (A of CN 101838757) optimization, and Iron and Steel Research Geueral Inst is newly developed
700 DEG C of level rotors are with proprietary alloy C700R1 (CN103866163 A).Compared with both alloys, the research and development of Haynes companies
The alloys of Haynes 282 (US8066938 B2) are due to intensity and enduring quality higher, being expected to be applied to higher temperature etc.
In level ultra supercritical coal-fired unit, such as U.S. has planned this materials application in 760 DEG C of ultra supercritical coal-fired units.Now
In ultra supercritical heat-resisting alloy, the alloys of Haynes 282 with its high intensity, enduring quality high, good heat endurance and welding
Performance, the emphasis material as various countries' research.But scientific research personnel has found in a large amount of meetings and document report：Except above-mentioned advantage
Outward, the Alloy At Room Temperature toughness (ballistic work) is poor.Its ballistic work is less than 30J after standard heat treatment state, and rapid after timeliness
Drop to 10J or so.The present inventor is to also further demonstrate the presence of this problem in the experimental studies of Haynes 282.
The poor toughness of Haynes 282 this problem seriously constrains it and is applied in actual industrial.Studies have reported that clearly referring to
Go out：" grain-boundary weakness and transgranular reinforcing are the main causes of the alloy ballistic works of Haynes 282 reduction.But, yet there are no can
The pertinent literature of the problem is solved, it is necessary to be furtherd investigate ".Therefore, face for 700 DEG C~760 DEG C steam parameters of satisfaction are super
The large component use requirement such as more complicated turbine rotor of operating mode in boundary's fired power generating unit, need badly develop it is more tough than Haynes 282
Property more preferably, the more preferable Chlorimet material of combination property.
The content of the invention
It is an object of the invention to provide a kind of ultra-supercritical steam turbine rotor high-strength and high ductility heat-resisting alloy and its preparation
Method, (at least to a great extent) solves above-mentioned technical problem, be it is a kind of have toughness more preferably, combination property it is preferably Ni-based
Heat-resisting alloy, is related to optimal components scope, processing technology and the Technology for Heating Processing of material, to meet 700 DEG C~760 DEG C steam ginsengs
The use requirement of the large component such as more complicated turbine rotor of operating mode in number ultra supercritical coal-fired unit.
To achieve the above object, (1) of the invention is theoretical theoretical with " selective reinforcement " right based on " multielement complex intensifying "
Alloying component carries out comprehensive optimization design：On the premise of avoiding timeliness harmful phase long to generate as far as possible, on the one hand by Co, Mo,
The reasonable addition of W, Nb element come realize alloy solid solution strengthen effect optimization；On the other hand containing for Al, Ti, Nb element is controlled
Measure and match to control the content of γ ', to reach the best match of solution strengthening and ageing strengthening；And strictly control C, Cr, Mo
Content control the form (interrupted shape distribution) of alloy grain boundary carbide, to ensure the grain-boundary strength and toughness of alloy；(2) tie
Large component material industry produce reality problem is closed, smelting-hot procedure is arranged in pairs or groups according to alloying component and heat processing technique
Most preferably set；(3) accuracy controlling is carried out to Technology for Heating Processing, to obtain optimal performance desired tissue：It is transgranular to separate out largely
γ ' of the average-size less than 30nm, grain boundaries carbide precipitate is interrupted shape.
Based on above-mentioned design principle, concrete technical scheme is as follows：
1st, the invention provides a kind of ultra-supercritical steam turbine rotor high-strength and high ductility heat-resisting alloy, its alloying component presses matter
Amount percentages contain：Carbon (C)：0.02~0.04%, chromium (Cr)：19.0~20.5%, molybdenum (Mo)：6.0~8.1%, cobalt
(Co):9.0~12.0%, tungsten (W)：0.10~0.50%, aluminium (Al)：1.40~1.60%, titanium (Ti)：1.55~1.95%,
Niobium (Nb)：0.10~0.60%, magnesium (Mg)：0.002~0.015%, zirconium (Zr)：0.002~0.01%, boron (B)：0.002~
0.008%, silicon (Si)：No more than 0.10%, manganese (Mn)：No more than 0.20%, sulphur (S)：No more than 0.002%, phosphorus (P)：No
More than 0.004%, balance of nickel (Ni).
Preferred Al+Ti mass percents meet：3.0%≤Al+Ti≤3.5%, and Ti/Al is than meeting 0.95≤Ti/
Al≤1.20。
In addition to alloy substrate nickel, above-mentioned main chemical compositions specifically choose the following (alloying component in this specification of reason
By mass percentage)：
Carbon：In Refractoloy C it is main in smelting, deformation processing and heat treatment process with other alloy element actions
Form carbide, such as MC, M23C6、M6C etc..These carbide are preferential to be separated out in crystal boundary, and the crystal boundary performance generation to material is important
Influence.On the one hand too high C has adverse effect on to the welding performance of material, on the other hand the too high C also companies of being also easy to produce
The continuous carbide for separating out.As Haynes 282 makes alloy that continuously distributed M is formed on crystal boundary by adding a large amount of C23C6Type carbon
Compound, that is, form so-called " stone wall " structure to improve creep strength.But numerous studies show：Continuously distributed carbonization
Thing toughness is poor；And the discontinuous carbide of graininess, can both prevent Grain Boundary Sliding and Crack Extension from improving creep rupture life, and
Rupture ductility and toughness can be improved.Therefore, the present invention is theoretical based on classical thermodynamics forming core, mainly by reducing carbide
Nuclear driving force reduces equiax crystal, with the carbide for obtaining discontinuously being distributed.Based on theoretical calculation, the addition for reducing carbon can
C content is strictly controlled to ensure grain-boundary strength and toughness effectively compared with the nuclear driving force of subcarbide, therefore in alloy of the present invention
System is in 0.02-0.04%.
Chromium：The most important element of the anti-steam corrosions of Cr.With the increase of Cr contents, its anti-steam corrosion performance substantially increases
Plus.But research shows, on the one hand excessive Cr can form the elevated temperature strength of α-Cr reduction materials；The addition of another aspect Cr can promote
Enter the formation of grain boundary carbide, be more likely formed sequential like carbide.Therefore steel of the present invention for meet anti-steam corrosion performance with
Grain boundary carbide form (interrupted shape) control requires that choosing Cr content ranges is:19.0~20.5%.
Molybdenum, Mo mainly plays solution strengthening effect in nickel-base alloy.Mo adds the High temperature diffusion speed that can slow down Al, Ti and Cr
Degree, improves Binding Forces Between Atoms in solid solution, slows down softening rate, significantly improves the heat resistance of heat-resisting alloy；But excess
On the one hand Mo can promote bulk M6The generation of c-type carbide, is on the other hand easily caused the intermetallic compound to form rich Mo, this
Two aspects can all cause the deterioration of material property.Therefore, there is no M after Pre-aging treatment to ensure alloy of the present invention6C-type is carbonized
Thing, and the M of richness Mo in timeliness long is avoided as far as possible6The generation of c-type carbide and intermetallic compound, Mo contents in alloy of the present invention
Strictly it is controlled to 6.0~8.1%.
Cobalt：Co is one of main solution strengthening element of nickel-base alloy, and Co addition matrixes can reduce the stacking fault energy of matrix,
Stacking fault energy reduction, the probability increase that fault occurs, makes the commutative Banach aglebra of dislocation more difficult, and so deformation is accomplished by outside bigger
Power, so as to reduce creep rate, improves creep resistance.But the Co of excess can form harmful intermetallic compound phase, material is reduced
The intensity of material.Therefore Co contents control of the present invention is 9.0~12.0%.
Tungsten：W mainly plays solution strengthening effect in nickel-base alloy, improves the creep fracture time of alloy.Because it is compared with Mo
With fusing point and lower diffusion coefficient higher, solid solution strengthening effect is stronger.The addition of W not only can effectively reduce Cr, Mo etc.
Diffusion coefficient of the carbide former in basic, can also reduce the diffusion in basic of the γ ' formation elements such as Al, Ti
Coefficient, reaches the purpose of reinforced alloys stabilizing tissue.But the W of excess not only reduces alloy hot-workability, and promotes metal
Between compound generation, reduce alloy strength.Therefore W content is 0.10~0.50% in alloy of the present invention.
Aluminium：Al primarily forms element for γ's '.The addition of Al can promote the precipitation of γ ', while Al can also improve alloy
Antioxygenic property.But excessive Al can form β-NiAl phases in nickel-base alloy.Therefore alloy Al content of the present invention for 1.40~
1.60%.
Titanium：Ti primarily forms element for γ's '.Ti is main to substitute in addition to dissolving in play solution strengthening effect substantially on a small quantity
γ’-Ni3Al atoms in Al phases, form Ni3(Al,Ti).Under conditions of certain Al content, as Ti contents increase, γ ' phases
Quantity increases, and alloy high-temp intensity increases.But excess Ti is added, and Ti/Al can be made too high, so that the opposite more stable η of γ '-
Ni3Ti phase in version.η-Ni3Ti is generally in tip-like, will deteriorate the performance of alloy.Therefore, from the control of the content and harmful phase of γ '
Controlling angle sets out, and with reference to the effect of Al elements, alloy of the present invention controls 1.55~1.95% Ti contents；Al and Ti is total simultaneously
In 3.0%≤Al+Ti≤3.5%, Ti/Al is than meeting 0.95≤Ti/Al≤1.20 for amount control.
Niobium：On the one hand Nb is the solution strengthening element in nickel-base alloy, and atomic radius is bigger than W and Mo, solution strengthening effect
Fruit becomes apparent from；On the other hand it is also main γ ' intensified elements, the mismatch of γ ' and matrix can be increased, improves the reinforcing of γ '
Effect, but can improve during γ ' coarsening rates make the high-temperature behavior of material under arms and accelerate to decline；Nb can also enter MC simultaneously
Phase, makes MC more stable, so that performance when reinforcing material is long；In addition low-alloyed antioxidant can also drop in Nb, and excess Nb pairings
The welding performance of gold has adverse effect on.Above-mentioned effect based on Nb, the addition of this alloy Nb considered based on solution strengthening,
Consider appropriate Nb with C-shaped on a small quantity compared with M simultaneously23C6、M6C more stable MC phases.Therefore alloy Nb contents control of the present invention exists
0.10~0.60%.
Magnesium：Mg is also a kind of important boundary-strengthening element, and on the one hand its Main Function is purification crystal boundary：Form high molten with S
The compound Mg S of point, reduces the illeffects of low melting point sulfide, improves alloy hot-workability；Mg is in segregation energy simultaneously
Crystal boundary energy, refinement and nodularization grain boundary carbide are reduced, increases crystal boundary adhesion, improve heat resistance.But the Mg of excess can produce low
Fusing point Ni-Mg phases, deteriorate hot-working character.Therefore, Mg contents are strict controlled in 0.002~0.015% in alloy of the present invention.
Zirconium：Zr is also a kind of important boundary-strengthening element.Zr can improve the adhesion of crystal boundary in Grain Boundary Segregation, reduce crystal boundary
Diffusion rate, strengthen crystal boundary.But when Zr contents are excessive, the carbide of Zr can be formed in grain boundaries, it is right as crack initiation source
Enduring quality has a negative impact.Therefore Zr controls are added in alloy of the present invention 0.002~0.015%.
Boron：B is a kind of important boundary-strengthening element, because its atomic size is small, it is easy to which segregation is in crystal boundary.When a small amount of B adds
Added-time, the creep rupture strength of alloy can be significantly improved.But when content exceedes a certain amount of, not only intercrystalline strengthening DeGrain can also shadow
Ring the welding performance to alloy.Therefore, B content is controlled 0.002~0.008% in alloy of the present invention.
Silicon：Si enrichment of element can reduce grain-boundary strength in crystal boundary, and it can promote σ phases to be separated out with Laves phases.Therefore, originally
Invention alloy is not added with Si, and the Si contents in furnace charge are limited within 0.1%.
Manganese：A small amount of Mn adds alloy melt chemical reaction can to occur by Mn and S and generate as a kind of refining agent
MnS, reduces the illeffects of S.Research is added less than 0.93% in being reported in Inconel 718 and Hastelloy X-alloys
Mn can improving welding property.But because Mn meeting segregations are in crystal boundary, weaken crystal boundary adhesion, reduce creep rupture strength.Therefore it is of the invention
In alloy by the control of Mn contents within 0.02%.
Sulphur：S is easy to be formed in crystal boundary the eutectic phase of low melting point, the hot-working character of the alloy that deteriorates significantly in nickel-base alloy
And elevated temperature strength, and influence weldability.Research shows that the presence of the element sulphur in Long-term Aging can also promote the generation of harmful phase.
Therefore, the sulfur content in this alloy needs to be strict controlled within 0.002%.
Phosphorus：The creep rupture strength of alloy can be improved there are some researches show micro P, but the addition of phosphorus can make HAZ liquation cracks incline
Need to be controlled within 0.004% to the phosphorus in increase, therefore this alloy.
Additionally, the performance to ensure alloy, five-harmful elementses and other impurity elements should be more low better.
2nd, the invention provides a kind of method for preparing invention alloy, the described method comprises the following steps：
(1) smelt：Smelting flow using the techniques of VIM+ESR+VAR tri- carries out alloy smelting, to ensure the pure of alloy
The uniformity of degree and material, so as to improve the mechanical property of material；
Homogenization Treatments：Alloying element is more in this alloy, easily formation element segregation, tissue odds in smelting process.Cause
This ingot casting need to use homogenization process to reduce composition and microstructure segregation, and the technique is based on remaining segregation coefficient δ formula：
Wherein, D is diffusion coefficient；L is secondary dendrite spacing；T is homogenization time.Based on above-mentioned formula, and further
Determine the Homogenization Treatments technique of alloy of the present invention for 1200 ± 10 DEG C are incubated 16~96 hours after engineering practice checking；
(2) forging technology：Alloy pig blank of the present invention is narrow due to hot processing temperature range window, to avoid forging as far as possible
The excessive problem for causing structural homogenity poor of part temperature difference in journey, the present invention uses soft sheathing process.Covering material is fibrofelt
With high temperature adhesive.Covering material is uniformly wrapped in 3~5 layers on forging, is effectively reduced heat and scatters and disappears, improved and become per fire
Shape amount, it is ensured that the structural homogenity and mechanical performance of forging；In substantial amounts of hot-compression experimental basis, by studying alloy
Deformation temperature, rate of deformation, dependent variable to forge complexity and forging after organize uniformity, and combine actual production come
Formulate forging technology：At 1055 DEG C~1175 DEG C, rate of deformation is 0.003~0.02s for forging temperature control-1。
(3) it is heat-treated：The heat treatment of alloy includes solution treatment and Ageing Treatment.Solution treatment is mainly used in precipitate and returns
Molten and grain size control, when usual grain size is 3-5 grades, alloy has optimal combination property.The present invention is true through experiment
The optimal solid solubility temperature of fixed this alloy is 1100~1145 DEG C, and the time is 1~4h, water quenching cooling；Ageing Treatment is mainly used in control
The γ ' of precipitated phase processed and the size and number of carbide.Optimal aging temp of the invention be defined as 745 DEG C~775 DEG C, time
It is 6~18h.
Beneficial effects of the present invention：Optimal components scope, smelting, processing by above-mentioned technical proposal to alloy of the present invention
Technique and Technology for Heating Processing are accurately limited, and alloy of the present invention can be made there was only MC types and M after standard heat treatment23C6Two kinds of type
Carbide, and grain boundary carbide is remarkably improved the plasticity and toughness of material in the distribution of interrupted shape；On the basis of solution strengthening simultaneously
Transgranular largely tiny (＜ 30nm) γ ' that separate out mutually can preferably be improved and be kept alloy strength.
Alloy structure feature after heat treatment：Transgranular to separate out γ ' of the average-size less than 30nm for a large amount of, grain boundaries are interrupted
Shape carbide, carbide only has MC types and M23C6Two kinds of carbide of type；Finally there is the alloy of the present invention with above-mentioned tissue
The characteristic of high-strength and high ductility, its performance can reach：
(1) room-temperature mechanical property：Tensile strength：Rm>=1100MPa, yield strength：Rp0.2>=680MPa, elongation：A≥
35%, the contraction percentage of area：Z >=35%, ballistic work：Akv≥50J；
(2) high temperature (700 DEG C) mechanical property：Tensile strength：Rm>=980MPa, yield strength：Rp0.2>=620MPa, elongation
Rate：A >=30%, the contraction percentage of area：Z >=30%；
Contrast other materials (detailed in Example), the strength grade of material of the present invention is high, and toughness (ballistic work) and plasticity are more
It is good, i.e., with more excellent combination property, it is adaptable to operating mode lower stress in 700 DEG C~760 DEG C level ultra supercritical coal-fired units
The large components such as complicated turbine rotor are used, with very wide application prospect.
Brief description of the drawings
Fig. 1 is the interrupted carbide SEM figures of crystal boundary after 1# embodiments are heat-treated.
Fig. 2 is transgranular tiny γ ' phases SEM figures after the heat treatment of 1# embodiments.
Fig. 3 is room temperature impact performance comparison figure in comparative example's alloy of the present invention.
Of the invention above-mentioned and/or additional aspect and advantage combination accompanying drawing to being will be apparent in the description of embodiment and
It is readily appreciated that.The accompanying drawing to be used needed for embodiment or description of the prior art will be briefly described, it is clear that；, retouch
Accompanying drawing in stating only embodiments of the invention, for those of ordinary skill in the art, are not paying creative work
On the premise of, other accompanying drawings can also be obtained according to the accompanying drawing for providing.
Specific embodiment
Below in conjunction with the accompanying drawing in the embodiment of the present invention, the embodiment of the present invention is described in detail.Obviously, it is described
Embodiment be only a part of embodiment of the invention, rather than whole embodiments.Based on the embodiment in the present invention, ability
The every other embodiment that domain those of ordinary skill is obtained under the premise of creative work is not made, belongs to guarantor of the present invention
The scope of shield.
Using technical solution of the present invention alloy property and strength grade highest Haynes 282 so far and developing
TOS1X-2 alloys carry out Performance comparision.Table 1 lists 4 kinds of Exemplary chemical compositions of compared steel, and wherein 1#, 2# is the present invention
The alloy of trial-production in alloys range, 3# is the Haynes 282 of Haynes companies of U.S. exploitation, and 4# is Japanese Toshiba's exploitation
TOS1X-2 alloys.As 1#, 2# embodiments of the invention, 3#, 4# are comparative example.VIM+ is used by 1#, 2# alloy manufacturing process
The techniques of ESR+VAR tri- smelt 200kg alloy pigs.Alloy pig is warming up into 1190 DEG C of insulations with stove carries out homogenization for 72 hours and moves back
Fire treatment, quick after coming out of the stove to carry out Soft Roll set, soft pack layer is 3 layers, is then carried out in 1055 DEG C~1175 DEG C temperature ranges many
Fire forging is become a useful person, and rate of deformation is 0.003~0.02s-1；Subsequent standards Technology for Heating Processing is：(1) solution treatment：1100℃/2
Water-cooled is to room temperature after hour；(2) Pre-aging treatment：Be heated to 755 DEG C insulation 10 hours after be air cooled to room temperature.3#, 4# alloy point
The standard heat treatment technique reported disclosed in document or technical report Cai Yong not corresponded to.
The alloying component (wt.%) of the comparative example of the present invention of table 1
The room temperature tensile properties of alloy in the comparative example of the present invention of table 2
700 DEG C of high temperature tensile properties of alloy in the comparative example of the present invention of table 3
Alloy properties data in alloy comparative example of the present invention are as shown in table 2, table 3, Fig. 3.From table 2 and table 3
It can be seen that：The room temperature strength of heat-resisting alloy of the present invention, high temperature, short time intensity and Haynes 282 quite, are closed better than TOS1X-2
Gold；And room temperature and high-temp plastic are superior to Haynes 282 and TOS1X-2.According to Fig. 3 it can further be seen that resistance to heat seal of the invention
Golden (embodiment 1# and 2#) room temperature impact work(is substantially better than comparative example 3# and 4# alloy, i.e., the toughness of alloy of the present invention is substantially better than
Alloy Haynes 282 and TOS1X-2.
In sum, the present invention is by alloying component precise control, the accurate limit of smelting, processing technology and Technology for Heating Processing
It is fixed, can make alloy of the present invention that there is the room-temperature mechanical property of heat-resisting alloy field highest ranking and high temperature, short time intensity so far, together
When also keep excellent plasticity and toughness, the i.e. characteristic with high-strength and high ductility, be 700 DEG C now~760 DEG C grade ultra supercriticals
The optimal Refractoloy of combination property in fired power generating unit, is nickel heat-resisting alloy field with very great application prospect
Another huge advance.
Although embodiments of the invention have been shown and described above, above-described embodiment is in the description of this specification
It is exemplary, it is impossible to be interpreted as limitation of the present invention, one of ordinary skill in the art do not depart from principle of the invention and
Above-described embodiment can be changed within the scope of the invention in the case of objective, changed, replaced and modification.
Claims (4)
1. ultra-supercritical steam turbine rotor high-strength and high ductility heat-resisting alloy, it is characterised in that：Alloying component is by mass percentage
Contain：C：0.02~0.04%, Cr：19.0~20.5%, Mo:6.0~8.1%, Co:9.0~12.0%, W：0.10~
0.50%, Al：1.40~1.60%, Ti：1.55~1.95%, Nb：0.10~0.60%, Mg：0.002~0.015%, Zr：
0.002~0.01%, B：0.002~0.008%, Si：No more than 0.10%, Mn：No more than 0.20%, S：No more than
0.002%, P：No more than 0.004%, balance of Ni.
2. heat-resisting alloy according to claim 1, it is characterised in that：Al+Ti mass percents meet：3.0%≤Al+Ti
≤ 3.5%, and Ti/Al mass percents meet 0.95≤Ti/Al≤1.20.
3. the preparation method of heat-resisting alloy described in a kind of claim 1 or 2, it is characterised in that：Processing step and control in process
The technical parameter of system is as follows：
(1) smelt and homogenization process：Smelting flow using the techniques of VIM+ESR+VAR tri- carries out alloy smelting, and ingot casting is uniform
Annealing technique is 1200 ± 10 DEG C and is incubated 16~96 hours；
(2) forging technology：Ingot formation and pyroplastic deformation using Soft Roll set technology forging, forging temperature control 1055 DEG C~
1175 DEG C, rate of deformation is in 0.003~0.02s-1Between；
(3) Technology for Heating Processing：Solution treatment+timeliness pretreatment, solid solution treatment process is 1100~1145 DEG C and is incubated 1~4 hour；
Aging treatment process is 745 DEG C -775 DEG C, and soaking time is 6~18h.
4. preparation method according to claim 3, it is characterised in that：The heat-resisting alloy for preparing have such as undertissue and
Performance：
Alloy structure feature after heat treatment：Transgranular to separate out γ ' of the average-size less than 30nm for a large amount of, grain boundaries are interrupted shape carbon
Compound, carbide only has MC types and M23C6Two kinds of carbide of type；
Room-temperature mechanical property meets：
Tensile strength：Rm≥1100MPa
Yield strength：Rp0.2≥680MPa
Elongation：A >=35%
The contraction percentage of area：Z >=35%
Ballistic work：Akv≥50J
700 DEG C of mechanicals behavior under high temperature of alloy meet：
Tensile strength：Rm≥980MPa
Yield strength：Rp0.2≥620MPa
Elongation：A >=30%
The contraction percentage of area：Z >=30%.
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| CN201710271511.0A CN106929710B (en) | 2017-04-24 | 2017-04-24 | Ultra-supercritical steam turbine rotor high-strength and high ductility heat-resisting alloy and preparation method thereof |
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