CN106929710B - 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
- Publication number
- CN106929710B CN106929710B CN201710271511.0A CN201710271511A CN106929710B CN 106929710 B CN106929710 B CN 106929710B CN 201710271511 A CN201710271511 A CN 201710271511A CN 106929710 B CN106929710 B CN 106929710B
- Authority
- CN
- China
- Prior art keywords
- alloy
- heat
- strength
- temperature
- resisting alloy
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- 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%
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
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%, surplus Ni.And Al+Ti mass percents meet：3.0%≤Al+Ti≤3.5%, Ti/Al mass percent meet 0.95≤Ti/Al≤1.20.The advantage is that can make the heat-resisting alloy of acquisition specific organization that there is the characteristic of high-strength and high ductility, it is suitable for the high temperature large components such as 700 DEG C~760 DEG C steam parameter extra-supercritical unit turbine rotors and uses.
Description
Technical field
The invention belongs to heat-resisting alloy technical fields, more particularly to a kind of ultra-supercritical steam turbine rotor high-strength and high ductility
It is contour to be suitable for 700 DEG C~760 DEG C steam parameter ultra supercritical coal-fired unit turbine rotors for heat-resisting alloy and preparation method thereof
Warm large component uses.
Background technology
With the development of society, demand of the human society to electric power is higher and higher.For China, thermal power output accounts for about
The 80% of national gross generation.It is expected that will be the most important hair in China or even the whole world in a very long time thermal power generation from now on
Electric mode.It is to improve the vapor (steam) temperature and pressure of unit to improve the most effective approach of the thermal efficiency.Countries in the world are being ground at first at present
Into 700 DEG C of steam parameter ultra supercritical power stations, the power generation thermal efficiency is estimated up to 50% or more.From beginning of this century America and Europe, day
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 is formal and carry out 700 DEG C
Ultra supercritical coal-fired unit technology national development plan.
With the raising of vapor (steam) temperature and pressure, ultra supercritical unit proposes relative keys heat proof material higher
Requirement.Usually under military service operating mode, material should meet：(1) 10 under service temperature5After hour, creep rupture strength is not less than
100MPa；(2) 2 × 10 in military service5Material 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) higher intensity, 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 cannot meet
The high temperature section component of requirement, generating set must select Refractoloy.
The Refractoloy developed at present is mainly divided to two classes：One kind is solution strengthening type alloy, and another kind of is that timeliness is strong
Change type alloy.For the more complicated large high-temperature component 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 (101838757 A of CN) optimization, and Iron and Steel Research Geueral Inst is newly developed
700 DEG C of grade rotors are with proprietary alloy C700R1 (CN103866163 A).Compared with both alloys, the research and development of Haynes companies
282 alloys of Haynes (US8066938 B2) are applied to higher temperature etc. due to higher intensity and enduring quality, being expected to
In grade ultra supercritical coal-fired unit, as the U.S. has planned this material being applied in 760 DEG C of ultra supercritical coal-fired units.Now
In ultra supercritical heat-resisting alloy, 282 alloys of Haynes are with its high intensity, high enduring quality, good thermal stability and welding
Performance becomes the emphasis material of various countries' research.But scientific research personnel has found in a large amount of meetings and document report：Except above-mentioned advantage
Outside, 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 demonstrating the presence of this problem in 282 experimental studies of Haynes.
This problem of 282 poor toughness of Haynes seriously constrains it and is applied in actual industrial.Studies have reported that clearly referring to
Go out：" grain-boundary weakness and it is transgranular reinforcing be 282 alloy ballistic works of Haynes reduce the main reason for.It can but yet there are no
The pertinent literature for solving the problems, such as this, is furtherd investigate ".Therefore, to meet, 700 DEG C~760 DEG C steam parameters are super to be faced
The large components requirement such as more complicated turbine rotor of operating mode in boundary's fired power generating unit, it is more tough than Haynes 282 there is an urgent need for developing
Property more preferably, the better Chlorimet material of comprehensive performance.
Invention content
The purpose of the present invention is to provide a kind of ultra-supercritical steam turbine rotor high-strength and high ductility heat-resisting alloys and its preparation
Method, (at least to a great extent) solve above-mentioned technical problem, be it is a kind of have toughness more preferably, comprehensive performance it is preferably Ni-based
Heat-resisting alloy is related to optimal components range, processing technology and the heat treatment process of material, to meet 700 DEG C~760 DEG C steam ginsengs
The requirement of the large components 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 it is theoretical theoretical right with " selective reinforcement " to be based on " multielement complex intensifying "
Alloying component carries out fully optimized design：Under the premise of avoiding long timeliness harmful phase to generate as possible, on the one hand by Co, Mo,
W, the reasonable of Nb elements is added to realize that alloy solid solution strengthens the optimization of effect；On the other hand containing for Al, Ti, Nb element is controlled
It measures and matches 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) it ties
Large component material industry produce reality problem is closed, according to alloying component to smelting-hot procedure collocation and heat processing technique
Most preferably set；(3) accuracy controlling is carried out to heat treatment process, to obtain optimal performance desired tissue：It is transgranular to be precipitated largely
Average-size is less than the γ ' of 30nm, and grain boundaries carbide precipitate is interrupted shape.
Based on above-mentioned design principle, specific technical solution is as follows：
1, the present invention provides a kind of ultra-supercritical steam turbine rotor high-strength and high ductility heat-resisting alloy, 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%, surplus is nickel (Ni).
Preferred Al+Ti mass percents meet：3.0%≤Al+Ti≤3.5%, and Ti/Al ratios meet 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 mainly in smelting, deformation processing and heat treatment process with other alloy element actions
Carbide is formed, such as MC, M23C6、M6C etc..These carbide are preferentially precipitated in crystal boundary, are generated to the crystal boundary performance of material important
Influence.On the one hand excessively high C has adverse effect on the welding performance of material, on the other hand the excessively high C also companies of being also easy to produce
The continuous carbide being precipitated.As Haynes 282 makes alloy form continuously distributed M on crystal boundary by adding a large amount of C23C6Type carbon
Compound forms so-called " stone wall " structure to improve creep strength.But numerous studies show：Continuously distributed carbonization
Object toughness is poor；And the discontinuous carbide of graininess, it can not only prevent Grain Boundary Sliding and crack propagation from improving creep rupture life, but also
Rupture ductility and toughness can be improved.For this purpose, the present invention is based on classical thermodynamics forming core theory, mainly passes through and reduce carbide
Nuclear driving force reduces equiax crystal, with the carbide being discontinuously distributed.Based on theoretical calculation, the additive amount for reducing carbon can
Effectively compared with the nuclear driving force of subcarbide, therefore C content is strictly controlled to ensure grain-boundary strength and toughness 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, anti-steam corrosion performance obviously increases
Add.But studies have shown that on the one hand excessive Cr can form α-Cr reduces the elevated temperature strength of material；The addition of another aspect Cr can promote
Into the formation of grain boundary carbide, sequential like carbide is made to be more likely formed.Therefore steel of the present invention be meet anti-steam corrosion performance with
Grain boundary carbide form (interrupted shape) control requires, and chooses Cr content ranges and is:19.0~20.5%.
Molybdenum, Mo mainly play solution strengthening effect in nickel-base alloy.The High temperature diffusion speed that can slow down Al, Ti and Cr is added in Mo
Degree improves Binding Forces Between Atoms in solid solution, slows down softening rate, significantly improve the heat resistance of heat-resisting alloy；But it is excessive
On the one hand Mo can promote bulk M6On the other hand the generation of c-type carbide is easy to cause the intermetallic compound to form rich Mo, this
Two aspects can all lead to the deterioration of material property.Therefore, there is no M after Pre-aging treatment for guarantee alloy of the present invention6C-type is carbonized
Object, and the M of richness Mo in long timeliness is avoided as possible6The generation of c-type carbide and intermetallic compound, Mo contents in alloy of the present invention
Stringent control is 6.0~8.1%.
Cobalt：Co is one of main solution strengthening element of nickel-base alloy, and matrix, which is added, in Co can reduce the stacking fault energy of matrix,
Stacking fault energy reduces, and the probability that fault occurs increases, and keeps the commutative Banach aglebra of dislocation more difficult, and deformation so just needs the outer of bigger
Power improves creep resistance to reduce creep rate.But excessive Co can form harmful intermetallic compound phase, reduce material
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.Since it is compared with Mo
With higher fusing point and lower diffusion coefficient, 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 achievees the purpose that reinforced alloys stabilizing tissue.But excessive W not only reduces alloy hot-workability, but also promote 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 alloy also can be improved in Al
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 additions, can make Ti/Al excessively high, to make the opposite more stable η-of γ '
Ni3Ti phase transition.η-Ni3Ti is in usually tip-like, will deteriorate the performance of alloy.Therefore, from the control of the content of γ ' and harmful phase
Controlling angle sets out, and in conjunction with the effect of Al elements, alloy of the present invention controls Ti contents 1.55~1.95%；Al and Ti is total simultaneously
Amount control meets 0.95≤Ti/Al≤1.20 in 3.0%≤Al+Ti≤3.5%, Ti/Al ratios.
Niobium：On the one hand Nb is the solution strengthening element in nickel-base alloy, atomic radius ratio W and Mo biggers, 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 γ ' coarsening rates makes the high-temperature behavior of material accelerate to decline during being on active service；Nb can also enter MC simultaneously
Phase keeps MC more stable, performance when long to reinforcing material；In addition low-alloyed antioxidant, and excessive Nb pairings can also drop in Nb
The welding performance of gold has adverse effect on.Above-mentioned effect based on Nb, the addition of this alloy Nb consider based on solution strengthening,
Consider that suitable Nb and C is formed on a small quantity compared with M simultaneously23C6、M6MC phases more stable C.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, on the one hand main function is purification crystal boundary：It is formed with S high molten
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, crystal boundary binding force is increased, improves heat resistance.But excessive Mg will produce low
Fusing point Ni-Mg phases, make hot-working character deteriorate.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.The binding force of crystal boundary can be improved in crystal boundary segregation by Zr, reduce crystal boundary
Diffusion rate, strengthen crystal boundary.But when Zr contents are excessive, the carbide of Zr can be formed in grain boundaries, becomes crack initiation source, it is right
Enduring quality has an adverse effect.Therefore addition Zr is controlled 0.002~0.015% in alloy of the present invention.
Boron：B is that a kind of important boundary-strengthening element is easy to segregation in crystal boundary since its atomic size is small.When a small amount of B adds
Added-time can significantly improve the creep rupture strength of alloy.But when content is more than a certain amount of, not only intercrystalline strengthening effect unobvious 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 precipitated 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：Alloy melt, which is added, in a small amount of Mn can be used as a kind of refining agent, and chemical reaction, which occurs, by Mn and S generates
MnS reduces the illeffects of S.Research is reported in Inconel 718 and Hastelloy X-alloys and is added less than 0.93%
Mn can improving welding property.But since Mn meeting segregations are in crystal boundary, weaken crystal boundary binding force, reduce creep rupture strength.Therefore the present invention
In alloy by the control of Mn contents within 0.02%.
Sulphur：S is easy to form the eutectic phase of low melting point, the hot-working character for the alloy that deteriorates significantly in crystal boundary 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：Some researches show that micro P, and the creep rupture strength of alloy can be improved, but the addition of phosphorus can make HAZ liquation cracks incline
Phosphorus to increase, therefore in this alloy need to control within 0.004%.
In addition, to ensure the performance of alloy, the lower five-harmful elements and other impurity elements should be the better.
2, it the present invention provides a kind of method preparing invention alloy, the described method comprises the following steps：
(1) it smelts：Flow is smelted using tri- techniques of VIM+ESR+VAR and carries out alloy smelting, to ensure the pure of alloy
The uniformity of degree and material, to improve the mechanical property of material；
Homogenization Treatments：Alloying element is more in this alloy, in smelting process easily formation element segregation, tissue odds.Cause
This ingot casting need to use homogenization process to reduce ingredient and microstructure segregation, which 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 that the Homogenization Treatments technique of alloy of the present invention is 1200 ± 10 DEG C and keeps the temperature 16~96 hours after engineering practice verification；
(2) forging technology：Alloy pig blank of the present invention is since hot processing temperature range window is narrow, to avoid forging as possible
The excessive problem for causing structural homogenity difference of part temperature difference in journey, the present invention use soft sheathing process.Covering material is fibrofelt
With high temperature adhesive.Covering material is uniformly wrapped in on forging 3~5 layers, heat loss can be effectively reduced, improves and becomes per fire
Shape amount ensures the structural homogenity and mechanical performance of forging；In a large amount of hot-compression experimental basis, by studying alloy
Deformation temperature, rate of deformation, dependent variable come to the uniformity organized after the complexity of forging and forging, and in conjunction with actual production
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 for precipitate and returns
Molten and grain size control, when usual grain size is 3-5 grades, alloy has best comprehensive performance.The present invention is true through testing
The best solid solubility temperature of this fixed alloy is 1100~1145 DEG C, and the time is 1~4h, water quenching cooling；Ageing treatment is mainly used for controlling
The γ ' of precipitated phase processed and the size and number of carbide.The best aging temp of the present invention is determined as 745 DEG C~775 DEG C, the time
For 6~18h.
Beneficial effects of the present invention：Pass through above-mentioned technical proposal is to the optimal components range of alloy of the present invention, smelting, processing
Technique and heat treatment process 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 are precipitated mutually preferably can improve and keep alloy strength.
Alloy structure feature after heat treatment：Transgranular that γs ' of the average-size less than 30nm are precipitated to be a large amount of, grain boundaries are interrupted
Shape carbide, carbide only have MC types and M23C6Two kinds of carbide of type；Finally make to have the alloy of the present invention of above-mentioned tissue to have
The characteristic of high-strength and high ductility, 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%；
Other materials (detailed in Example) is compared, the strength grade of material of the present invention is high, and toughness (ballistic work) and plasticity are more
It is good, that is, there is more excellent comprehensive performance, the operating mode lower stress suitable for 700 DEG C~760 DEG C grade ultra supercritical coal-fired units
The large components such as complicated turbine rotor use, and have very wide application prospect.
Description of the drawings
Fig. 1 is the carbide SEM figures that crystal boundary is interrupted 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 alloy of the present invention.
The above-mentioned and/or additional aspect and advantage combination attached drawing of the present invention to will be apparent in the description of embodiment and
It is readily appreciated that.By a brief introduction will be made to the drawings that need to be used in the embodiment or the description of the prior art, it is clear that；, retouch
Attached drawing in stating is only the embodiment of the present invention, for those of ordinary skill in the art, is not being made the creative labor
Under the premise of, other attached drawings can also be obtained according to the attached drawing of offer.
Specific implementation mode
Following will be combined with the drawings in the embodiments of the present invention, and the embodiment of the present invention is described in detail.Obviously, described
Embodiment be only a part of the embodiment of the present invention, instead of all the embodiments.Based on the embodiments of the present invention, ability
The every other embodiment that domain those of ordinary skill is obtained without making creative work, belongs to guarantor of the present invention
The range of shield.
Using technical solution of the present invention alloy property and the highest Haynes 282 of strength grade so far and developing
TOS1X-2 alloys carry out performance comparison.Table 1 lists the Exemplary chemical ingredient of 4 kinds of compared steels, and wherein 1#, 2# is the present invention
The alloy manufactured experimently in alloys range, 3# are the Haynes 282 of Haynes companies of U.S. exploitation, and 4# is Japanese Toshiba's exploitation
TOS1X-2 alloys.As 1#, 2# the embodiment of the present invention, 3#, 4# are comparative example.VIM+ is used by 1#, 2# alloy manufacturing process
Tri- techniques of ESR+VAR smelt 200kg alloy pigs.It alloy pig with stove is warming up to 1190 DEG C of heat preservations carries out within 72 hours homogenization and move back
Fire processing quickly carries out Soft Roll set after coming out of the stove, soft pack layer is 3 layers, is then carried out in 1055 DEG C~1175 DEG C temperature ranges more
Fire forging is become a useful person, and rate of deformation is 0.003~0.02s-1；Subsequent standards heat treatment process is：(1) solution treatment：1100℃/2
Water cooling is to room temperature after hour；(2) Pre-aging treatment：Be heated to 755 DEG C heat preservation 10 hours after be air-cooled to room temperature.3#, 4# alloy point
The standard heat treatment technique that report is disclosed in document or technical report Cai Yong not corresponded to.
The alloying component (wt.%) of 1 comparative example of the present invention of table
The room temperature tensile properties of alloy in 2 comparative example of the present invention of table
700 DEG C of high temperature tensile properties of alloy in 3 comparative example of the present invention of table
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：Room temperature intensity, high temperature, short time intensity and the Haynes 282 of heat-resisting alloy of the present invention are suitable, 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 the resistance to heat seal of the present 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 conclusion the present invention is accurately controlled by alloying component, smelt, the accurate limit of processing technology and heat treatment process
It is fixed, it can make alloy of the present invention that there is the room-temperature mechanical property of heat-resisting alloy field highest level and high temperature, short time intensity so far, together
When also keep excellent plasticity and toughness, i.e. the characteristic with high-strength and high ductility is 700 DEG C now~760 DEG C grade ultra supercriticals
The best Refractoloy of comprehensive performance in fired power generating unit has very great application prospect, is nickel heat-resisting alloy field
Huge advance again.
Although the embodiments of the present invention has been shown and described above, above-described embodiment is in the description of this specification
Illustratively, be not considered as limiting the invention, those skilled in the art do not depart from the principle of the present invention and
It can make changes, modifications, alterations, and variations to the above described embodiments within the scope of the invention in the case of objective.
Claims (2)
1. a kind of ultra-supercritical steam turbine rotor high-strength and high ductility heat-resisting alloy, it is characterised in that：Alloying component presses quality percentage
Contain than meter：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：It is not more than
0.002%, P：No more than 0.004%, surplus Ni；
Al+Ti mass percents meet：3.0%≤Al+Ti≤3.5%, and Ti/Al mass percents meet 0.95≤Ti/Al
≤1.20；Grain boundaries are interrupted shape carbide simultaneously.
2. the preparation method of heat-resisting alloy described in a kind of claim 1, it is characterised in that：It processing step and in process controls
Technical parameter is as follows：
(1) smelting and homogenization process：Flow is smelted using tri- techniques of VIM+ESR+VAR and carries out alloy smelting, ingot casting is uniform
Annealing technique is 1200 ± 10 DEG C and keeps the temperature 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) heat treatment process：Solution treatment+timeliness pretreatment, solid solution treatment process are 1100~1145 DEG C and keep the temperature 1~4 hour；
Aging treatment process is 745 DEG C -775 DEG C, and soaking time is 6~18h；
The heat-resisting alloy being prepared has such as undertissue and performance：
Alloy structure feature after heat treatment：It is transgranular that γs ' of the average-size less than 30nm, the interrupted shape carbonization of grain boundaries is precipitated to be a large amount of
Object 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%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| 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 |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| 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 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN106929710A CN106929710A (en) | 2017-07-07 |
| CN106929710B true CN106929710B (en) | 2018-11-09 |
Family
ID=59438096
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201710271511.0A Active 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 |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN106929710B (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2019125637A2 (en) * | 2017-11-10 | 2019-06-27 | Haynes International, Inc. | HEAT TREATMENTS FOR IMPROVED DUCTILITY OF Ni-Cr-Co-Mo-Ti-Al ALLOYS |
| CN108441704A (en) * | 2018-03-15 | 2018-08-24 | 江苏理工学院 | A kind of Refractoloy material and its preparation process |
| CN116287867A (en) * | 2022-09-07 | 2023-06-23 | 中国联合重型燃气轮机技术有限公司 | Bending crack-free nickel-based superalloy, and preparation method and application thereof |
| CN115449669B (en) * | 2022-09-13 | 2023-08-08 | 中国联合重型燃气轮机技术有限公司 | Creep-resistant and oxidation-resistant nickel-based superalloy, and preparation method and application thereof |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20090321405A1 (en) * | 2008-06-26 | 2009-12-31 | Huntington Alloys Corporation | Ni-Co-Cr High Strength and Corrosion Resistant Welding Product and Method of Preparation |
| CN102628127A (en) * | 2012-05-03 | 2012-08-08 | 丹阳恒庆复合材料科技有限公司 | High-strength corrosion-resisting nickel base alloy and manufacturing method thereof |
| CN103060616B (en) * | 2012-12-25 | 2015-01-21 | 钢铁研究总院 | Nickel-base heat-resisting alloy |
| CN103361518B (en) * | 2013-06-11 | 2015-04-08 | 太原钢铁(集团)有限公司 | Nickel-based seamless pipe for ultra supercritical boiler and manufacturing method thereof |
| CN105112728B (en) * | 2015-09-29 | 2017-03-22 | 钢铁研究总院 | Heat-resisting alloy for 700-DEG C ultra-supercritical steam turbine rotor and preparation method thereof |
-
2017
- 2017-04-24 CN CN201710271511.0A patent/CN106929710B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN106929710A (en) | 2017-07-07 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108315599B (en) | A kind of high cobalt nickel base superalloy and preparation method thereof | |
| CN105112728B (en) | Heat-resisting alloy for 700-DEG C ultra-supercritical steam turbine rotor and preparation method thereof | |
| CN106929710B (en) | Ultra-supercritical steam turbine rotor high-strength and high ductility heat-resisting alloy and preparation method thereof | |
| CN103045962B (en) | Steel for steam-temperature ultra-supercritical thermal power unit and preparation method thereof | |
| CN104630597B (en) | A kind of iron nickel and chromium high temperature alloy and its manufacture method | |
| CN108467972A (en) | A kind of ni-base wrought superalloy and preparation method thereof of bearing high temperature ability | |
| CN102628127A (en) | High-strength corrosion-resisting nickel base alloy and manufacturing method thereof | |
| JPH0563544B2 (en) | ||
| CN104718306A (en) | Austenitic steel alloy having excellent creep strength and resistance to oxidation and corrosion at elevated use temperatures | |
| CN105849302A (en) | Steel for low-temperature service having excellent surface processing quality | |
| JP7009618B2 (en) | Steel for ultra-supercritical thermal power generator group and its manufacturing method | |
| CN101476088A (en) | R17Cr1Ni3Mo steel for nuclear pressure vessel and preparation thereof | |
| JP4222705B2 (en) | Manufacturing method of high purity high Cr ferritic heat resistant steel and high purity high Cr ferritic heat resistant steel | |
| CN108715951B (en) | Multiphase-structure nickel-chromium-iron-series high-temperature alloy and preparation method thereof | |
| US11242585B2 (en) | Iron-based superalloy for high temperature 700 ° C. with coherent precipitation of cuboidal B2 nanoparticles | |
| CN108866389A (en) | A kind of high strength and low cost corrosion and heat resistant nickel base superalloy and its preparation process and application | |
| CN103667967A (en) | Heat-resistant steel for ultra-supercritical steam turbine rotor | |
| JP2012107328A (en) | Polycrystal nickel-based heat-resistant superalloy excellent in mechanical property at high temperature | |
| CN108103400A (en) | Maraging steel of compound precipitation strength and preparation method thereof between a kind of nano level metal | |
| US6761854B1 (en) | Advanced high temperature corrosion resistant alloy | |
| CN111112878A (en) | Bright welding wire for heat-resistant steel of ultra-supercritical coal-fired power station | |
| CN109536841A (en) | A kind of corrosion resistant austenite-ferrite two-phase heat resisting steel and preparation method thereof | |
| CN104651743A (en) | Multielement composite heat-resistant steel | |
| CN102691016B (en) | Precipitation hardenable high temperature steel | |
| CN102634741A (en) | High-temperature heat-resistant and corrosion-resistant stainless steel and manufacturing method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |