CN105821250A - High-strength nickel-base superalloy and manufacturing method thereof - Google Patents
High-strength nickel-base superalloy and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses a high-strength nickel-base superalloy and its manufacturing method. the alloy contains the following ingredients (by weight): 0.02-0.08% of C, 14.0-17.0% of Cr, 5.0-9.0% of Fe, 0.50-1.30% of Al, 2.25-2.75% of Ti, 0.7-1.2% of Nb, 0.02-1.0% of Mn, 0.001-0.006% of Mg, 0.001-0.03% of Ce, 0.01-0.06% of Zr, S being less than or equal to 0.005%, P being less than or equal to 0.008%, Si being less than or equal to 0.30%, Cu being less than or equal to 0.30%, and the rest of nickel and unavoidable impurities. The manufacturing method of the alloy comprises vacuum induction melting and heat treatment. The invention has the following advantages: failure of components and parts during using process can be remarkably reduced, and the product of the invention has a good application prospect.
Description
Technical field
The present invention relates to a kind of high-strength nickel based high-temperature alloy and manufacture method thereof, belong to metal smelt technical field.
Background technology
High temperature alloy refers to bear certain stress 600 DEG C of temperatures above and have a class alloy of antioxidation and corrosion resistance.Iron-based, Ni-based and cobalt-based can be divided into by matrix.Wherein nickel base superalloy is with the antioxidant anticorrosive performance of its excellence, and the elevated temperature strength of excellence and be widely used in the fields such as Aero-Space electromotor, gas turbine, oil gas field, auto industry.The performance of high temperature alloy depends on alloying component, manufacturing process system, and wherein elevated temperature strength, antioxidant anticorrosive performance are the most important performances of high temperature alloy, and it is finally decided by the microscopic structure state of finished steel.Along with scientific and technological progress, people have higher requirement for temperature capability, the combination property (antioxidant anticorrosive, elevated temperature strength, high-temperature and durable plasticity etc.) of high temperature alloy, and this can be realized by the Technology for Heating Processing of the design of alloying component, new smelting process and optimization.
(the Unite States Standard trade mark is UNSN00750 to InconelX-750 alloy, domestic for GH4145 alloy), its standard analysis is as shown in table 1, owing to having higher intensity, good anti-corrosion property at high temperature, it is widely used in the elastic component in gas turbine or boiling water nuclear reactor or securing member, such as bolt, rivet, spring etc..But, after utilizing this alloy to manufacture high temperature force-summing element, in use crystal boundary becomes weak link, and catastrophic failure when not occurring substantially to deform, and greatly affects the safety in utilization of equipment.Being found by experimental study, show as in the performance indications of alloy, the middle temperature rupture ductility (such as 730 DEG C/345MPa) of this alloy is on the low side, and often less than 5%, it is susceptible to deformation failure during use.Therefore, it is necessary to this alloy is carried out composition and manufacturing process is optimized.
The standard analysis of table 1InconelX-750 alloy
| C | Cr | Fe | Al | Ti | Nb | Mn | S | Si | P | Cu |
| ≤0.08 | 14.0-17.0 | 5.0-9.0 | 0.40-1.0 | 2.25-2.75 | 0.7-1.2 | ≤1.0 | ≤0.01 | ≤0.50 | ≤0.015 | ≤0.5 |
A kind of nickel-base alloy is provided, including following components in percentage by weight: 77～the nickel of 82% in literature query and patent retrieval, CN201210457802.6 patent application；17～the chromium of 22%；The cerium of not higher than 0.3%；The ferrum of surplus and inevitable impurity.This alloy is by with the addition of rare-earth element cerium, and to reach crystal grain thinning and to improve oxidation resistance effect, but this alloy is the most single due to composition, although has good non-oxidizability, but is unable to reach high intensity requirement.Additionally Chinese patent CN102766787A relates to the class nickel-base alloy for gas turbine application, this alloy contains the cobalt (5-10%) of high level, separately with the addition of noble element hafnium, relatively costly, additionally with the addition of the boron of daughter element in absorption, it is impossible to be applied in boiling water nuclear reactor.Chinese patent CN1151191 mono-kind improves high temperature alloy creep resistance, fatigue properties and the method for stress breaking life, and thus obtained alloy.The method includes being adjusted to alloy containing (by weight) 0.012-0.05%P, less than 0.1%C, with less than 0.03%B.Compound P, B of adding can improve the enduring quality (such as Inconel718) of part nickel-base alloy, but for being similar to X-750 alloy, P is harmful element, can significantly reduce serviceability, additionally add the boron of daughter element in more absorption, it is impossible to be applied in the devices such as boiling water nuclear reactor.
Summary of the invention
It is an object of the invention to provide a kind of high intensity nickel base high temperature alloy composition, with and preparation method thereof introduction.This alloy is compared with homologous series alloy, the Reasonable adjustment content range of the elements such as Al, Mn, it is combined and with the addition of the micro alloying elements such as Mg, Ce, Zr, after using rational hot-working and Technology for Heating Processing, final finished can obtain higher intensity, and there is good middle temperature rupture ductility, can effectively reduce inefficacy in use.
For achieving the above object, the technical scheme is that
A kind of high-strength nickel based high-temperature alloy, described alloy includes the following component of percentage: C:0.02～0.08%；Cr:14.0～17.0%；Fe:5.0～9.0%；Al:0.50～1.30%；Ti:2.25～2.75%；Nb:0.7～1.2%；Mn:0.02～1.0%；Mg:0.001～0.006%；Ce:0.001～0.03%；Zr:0.01～0.06%；S≤0.005%；P≤0.008%；Si≤0.30%；Cu≤0.30%, surplus is nickel and inevitable impurity.
Below the present invention is had the excellent chemical composition of thermoplasticity nickel base superalloy and the reason of span of control is explained as follows:
C:0.02-0.08%
C is the indispensable element that in nickel base superalloy, carbide is formed.It is necessary that C controls at 0.02-0.08%, one to ensure that a number of carbide separates out at crystal boundary, playing a part crystal grain thinning, improve creep rupture strength and plasticity, two to prevent too much carbide from causing field trash too much and segregation tendency, cause crystal grain uneven and alloy plasticity deteriorates.Consider C content to control at 0.02-0.08%.
Cr:14.0-17.0%
Ni-Cr-Fe alloy constitutes the matrix of this nickel-base alloy, the addition of Cr element considers two factors, and one is to ensure that formation single phase austenite solid solution, and two are intended to consider corrosion resistance, Cr is to improve the maximally effective element of alloy corrosion resistance, considers and controls Cr content at 14.0-17.0%.
Ni: >=70%
Ni-Cr-Fe alloy constitutes the matrix of this nickel-base alloy, and Fe addition about 7%.Appropriate Fe adds, and can replace part Ni, the not performance of appreciable impact alloy, can significantly reduce cost of alloy.But, too much Fe, the stability for alloy is unfavorable, considers, and Ni content is necessary >=and 70%.
Al:0.5～1.3%
Al be in nickel-base alloy phase must form element, and be most important a kind of hardening constituent in nickel-base alloy mutually.By controlling suitable Al, some tissues can be separated out, by forming coherence or the relation of half coherence with matrix solid solution, and then form strengthening.Meanwhile, the antioxygenic property for alloy that adds of Al is significantly improved, and at high temperature Al with O2 reacts, and forms one layer of fine and close Al2O3 oxide-film, and alloy is formed protection.Al content is the highest, and the amount of precipitation of phase is the biggest, but Al is too high can increase the hot worked difficulty of alloy, makes material easily crack.So Al controls at 0.5-1.3%.
Ti:2.25～2.75%
Containing higher Ti in this alloy, it is because Ti in alloy and is easy to dissolve in phase, can substitute for the Al atom of 2/3rds.After Ti enters, making precipitation slow down, effectively stop the effect of overaging, this effect makes alloy be suitable in high-temperature work environment to use for a long time.But Ti adds too much will create Ni3Ti (η phase), and Ni3Ti phase is without age hardening capability, and this alloy Ti is containing measuring span of control at Ti:2.25-2.75%.
Nb:0.7～1.2%
This alloy adds a certain amount of Nb, is because Nb Yu Ni and forms hardening constituent, significantly increase the intensity of alloy, it addition, slightly higher Nb can put forward heavy alloyed high-temperature stability.But, Nb adds too much, owing to Nb element ratio is great, easily forms segregation in smelting process, as produced the metallurgical imperfections such as black speck.This alloy Nb is containing measuring span of control at 0.7-1.2%.
Mn:0.02～1.0%
Alloy adds a small amount of Mn, additionally can have certain deoxidation in steelmaking process with crystal grain thinning.But, too much Mn element adds membership segregation and with joint efforts, significantly reduces alloy enduring quality in crystal boundary, weakening Grain-boundary Junctions.This alloy Mn content controls at 0.02-1.0%.
Mg:0.001～0.006%
Due to the Mg element added in alloy, it is mainly distributed on grain boundaries, and Mg Yu S has the strongest adhesion, and then the segregation of reduction grain boundaries S, can be substantially improved the thermoplasticity of alloy.But, Mg too high levels, mechanical property is adversely affected.
Ce:0.001～0.03%
The addition of Ce, on the one hand has deoxidation and desulfidation as cleanser, reduces oxygen and the sulfur illeffects at crystal boundary；On the other hand can improve the non-oxidizability of alloy as active element, improve surface stability.
Zr:0.01～0.06%
The Zr element added in this alloy, segregation to crystal boundary, reduces grain boundary defects, improves Grain-boundary Junctions and make a concerted effort, reduce grain boundary decision speed, thus slow down dislocation climb, strengthen crystal boundary.Meanwhile, Zr segregation can reduce interface energy in crystal boundary, improves Grain-Boundary Phase form, reduces the size of Grain-Boundary Phase, improves creep rupture life, improves rupture ductility.
S, P are as the harmful element of this alloy, and its content is the lowest more good, simultaneously takes account of alloy manufacturing cost, is controlled in S≤0.005；In the range of P≤0.008.
Other element, as, Si, Cu etc., be the non-beneficial element being difficult in this alloy avoid completely, content increase after can be susceptible to segregation, affect the performance of alloy, simultaneously take account of alloy manufacturing cost, controlled in Si≤0.30；In the range of Cu≤0.30.
A kind of manufacture method of high-strength nickel based high-temperature alloy as described in the present invention, including smelting step and heat treatment step, wherein, smelting step is that vacuum induction smelting adds electroslag remelting or vacuum induction is smelted and added vacuum consumable remelting, and heat treatment step is that hammer cogging is become a useful person or Forge Heating rolls into material.
Preferably, after the steel ingot obtained after described smelting is incubated at 1100～1200 DEG C, carries out hammer cogging or be rolled into dish circle；Opening forging or start rolling temperature is: 1050～1150 DEG C, finish-forging or finishing temperature >=900 DEG C, after forging or roll rear air cooling to room temperature.
Preferably, described heat-treating methods includes solution treatment and Ageing Treatment, and wherein, described solution treatment is by the air cooling after 1120～1140 DEG C of insulations 2 hours of the rerolled steel after forging or after rolling；Described Ageing Treatment be the steel semi-finished product after solution treatment are incubated 24 hours at 835～855 DEG C after, after being cooled to 695～715 DEG C in 2 hours, be incubated 20 hours, air cooling.
Preferably, described remelting processing parameter setting is limited to occur without metallurgical segregation in final steel ingot or finished product material.
After have employed technique scheme, the present invention has the advantages that: compared with existing X-750 alloy, have adjusted the contents level of Al, Mn element, reduce S, P impurity content, and the compound interpolation of logical Mg, Ce, Zr element, after using rational hot-working and Technology for Heating Processing, higher-strength and plasticity coupling can be obtained, substantially improve alloy middle temperature plasticity simultaneously, middle temperature rupture ductility stability contorting under 730 DEG C/345MPa is more than 8%, parts inefficacy in use can be substantially reduced, there is good application prospect.
Detailed description of the invention
Below in conjunction with embodiment, the invention will be further described, but protection scope of the present invention is not only limited to embodiment.
Embodiment 1:
One, according to the formula dispensing in table 2, control C is 0.079%, Cr is 15.3%, Fe is 7.11%, Mn is 0.04%, Nb is 1.01%, Al is 0.79%, Ti is 2.57%, P is 0.007%, S is 0.003%, Si is 0.06%, Cu is 0.03%, Mg is 0.003%, Ce is 0.0028%, Zr is 0.046%, and surplus is nickel and inevitable impurity.
Two, by vacuum induction melting and be cast into Φ 290 electrode, electrode obtains Φ 400 steel ingot after argon shield electroslag or vacuum consumable remelting.Wherein remelting processing parameter sets, and such as molten speed etc., is limited occurring without metallurgical segregation in final steel ingot or finished product material.
Three, after Heating Steel Ingots is incubated at least 2h to 1100～1200 DEG C, carrying out hammer cogging, cogging is 120 side's strip plates.Opening forging temperature is: 1050～1150 DEG C, final forging temperature >=900 DEG C, after forging, air cooling is to room temperature.
Four, after strip plate is heated to 1100～1200 DEG C of insulation time enough, carries out rolling and become a useful person, be rolled into 55-80mm bar.Start rolling temperature is: 1050～1150 DEG C, finishing temperature >=900 DEG C, rolls rear air cooling to room temperature.
Five, bar Technology for Heating Processing is: solution treatment: 1l20～2 hours air coolings of 1140 DEG C of insulations.Ageing Treatment: 835～855 DEG C are incubated 24 hours, in 2 hours, stove is cooled to 20 hours air coolings of 695～715 DEG C of insulations.
Embodiment 2:
One, according to the formula dispensing in table 2, control C is 0.050%, Cr is 15.4%, Fe is 8.21%, Mn is 0.36%, Nb is 1.06%, Al is 0.74%, Ti is 2.53%, P is 0.007%, S is 0.003%, Si is 0.05%, Cu is 0.02%, Mg is 0.002%, Ce is 0.0024%, Zr is 0.045%, and surplus is nickel and inevitable impurity.
Two, by vacuum induction melting and be cast into Φ 290 electrode, electrode obtains Φ 400 steel ingot after argon shield electroslag or vacuum consumable remelting.Wherein remelting processing parameter sets, and such as molten speed etc., is limited occurring without metallurgical segregation in final steel ingot or finished product material.
Three, after Heating Steel Ingots to 1100～1200 DEG C insulation time enough, carrying out hammer cogging, cogging is 120 side's strip plates.Opening forging temperature is: 1050～1150 DEG C, final forging temperature >=900 DEG C, after forging, air cooling is to room temperature.
Four, strip plate be heated to 1100～1200 DEG C be incubated at least 2h after, carry out rolling and become a useful person, be rolled into 55～80mm bars.Start rolling temperature is: 1050～1150 DEG C, finishing temperature >=900 DEG C, rolls rear air cooling to room temperature.
Five, bar Technology for Heating Processing is: solution treatment: 1l20～2 hours air coolings of 1140 DEG C of insulations.Ageing Treatment: 835～855 DEG C are incubated 24 hours, in 2 hours, stove is cooled to 20 hours air coolings of 695～715 DEG C of insulations.
Embodiment 3:
One, according to the formula dispensing in table 2, control C is 0.052%, Cr is 15.5%, Fe is 6.78%, Mn is 0.05%, Nb is 1.05%, Al is 0.89%, Ti is 2.27%, P is 0.006%, S is 0.002%, Si is 0.02%, Cu is 0.03%, Mg is 0.003%, Ce is 0.0042%, Zr is 0.040%, and surplus is nickel and inevitable impurity.
Two, by vacuum induction melting and be cast into Φ 290 electrode, electrode obtains Φ 400 steel ingot after argon shield electroslag or vacuum consumable remelting.Wherein remelting processing parameter sets, and such as molten speed etc., is limited occurring without metallurgical segregation in final steel ingot or finished product material.
Three, after Heating Steel Ingots is incubated at least 2h to 1100～1200 DEG C, carrying out hammer cogging, cogging is 120 side's strip plates.Opening forging temperature is: 1050～1150 DEG C, final forging temperature >=900 DEG C, after forging, air cooling is to room temperature.
Four, after strip plate is heated to 1100～1200 DEG C of insulation time enough, carries out rolling and become a useful person, be rolled into 55～80mm bars.Start rolling temperature is: 1050～1150 DEG C, finishing temperature >=900 DEG C, rolls rear air cooling to room temperature.
Five, bar Technology for Heating Processing is: solution treatment: 1l20～2 hours air coolings of 1140 DEG C of insulations.Ageing Treatment: 835～855 DEG C are incubated 24 hours, in 2 hours, stove is cooled to 20 hours air coolings of 695～715 DEG C of insulations.
Embodiment 4:
One, according to the formula dispensing in table 2, control C is 0.032%, Cr is 15.5%, Fe is 6.44%, Mn is 0.70%, Nb is 1.00%, Al is 0.82%, Ti is 2.54%, P is 0.004%, S is 0.004%, Si is 0.07%, Cu is 0.03%, Mg is 0.003%, Ce is 0.0030%, Zr is 0.030%, and surplus is nickel and inevitable impurity.
Two, by vacuum induction melting and be cast into Φ 290 electrode, electrode obtains Φ 400 steel ingot after argon shield electroslag or vacuum consumable remelting.Wherein remelting processing parameter sets, and such as molten speed etc., is limited occurring without metallurgical segregation in final steel ingot or finished product material.
Three, after Heating Steel Ingots is incubated at least 2h to 1100～1200 DEG C, carrying out hammer cogging, cogging is 120 side's strip plates.Opening forging temperature is: 1050～1150 DEG C, final forging temperature >=900 DEG C, after forging, air cooling is to room temperature.
Four, after strip plate is heated to 1100～1200 DEG C of insulation time enough, carries out rolling and become a useful person, be rolled into 55～80mm bars.Start rolling temperature is: 1050～1150 DEG C, finishing temperature >=900 DEG C, rolls rear air cooling to room temperature.
Five, bar Technology for Heating Processing is: solution treatment: 1l20～2 hours air coolings of 1140 DEG C of insulations.Ageing Treatment: 835～855 DEG C are incubated 24 hours, in 2 hours, stove is cooled to 20 hours air coolings of 695～715 DEG C of insulations.
Embodiment 5:
One, according to the formula dispensing in table 2, control C is 0.030%, Cr is 15.3%, Fe is 7.00%, Mn is 0.10%, Nb is 0.98%, Al is 0.87%, Ti is 2.60%, P is 0.005%, S is 0.005%, Si is 0.02%, Cu is 0.02%, Mg is 0.002%, Ce is 0.0041%, Zr is 0.032%, and surplus is nickel and inevitable impurity.
Two, by vacuum induction melting and be cast into Φ 290 electrode, electrode obtains Φ 400 steel ingot after argon shield electroslag or vacuum consumable remelting.Wherein remelting processing parameter sets, and such as molten speed etc., is limited occurring without metallurgical segregation in final steel ingot or finished product material.
Three, after Heating Steel Ingots is incubated at least 2h to 1100～1200 DEG C, carrying out hammer cogging, cogging is 120 side's strip plates.Opening forging temperature is: 1050～1150 DEG C, final forging temperature >=900 DEG C, after forging, air cooling is to room temperature.
Four, after strip plate is heated to 1100～1200 DEG C of insulation time enough, carries out rolling and become a useful person, be rolled into 55～80mm bars.Start rolling temperature is: 1050～1150 DEG C, finishing temperature >=900 DEG C, rolls rear air cooling to room temperature.
Five, bar Technology for Heating Processing is: solution treatment: 1l20～2 hours air coolings of 1140 DEG C of insulations.Ageing Treatment: 835～855 DEG C are incubated 24 hours, in 2 hours, stove is cooled to 20 hours air coolings of 695～715 DEG C of insulations.
Embodiment 6:
One, according to the formula dispensing in table 2, control C is 0.035%, Cr is 15.9%, Fe is 6.98%, Mn is 0.16%, Nb is 0.96%, Al is 0.78%, Ti is 2.56%, P is 0.005%, S is 0.003%, Si is 0.10%, Cu is 0.02%, Mg is 0.004%, Ce is 0.0029%, Zr is 0.024%, and surplus is nickel and inevitable impurity.
Two, by vacuum induction melting and be cast into Φ 290 electrode, electrode obtains Φ 400 steel ingot after argon shield electroslag or vacuum consumable remelting.Wherein remelting processing parameter sets, and such as molten speed etc., is limited occurring without metallurgical segregation in final steel ingot or finished product material.
Three, after Heating Steel Ingots is incubated at least 2h to 1100～1200 DEG C, carrying out hammer cogging, cogging is 120 side's strip plates.Opening forging temperature is: 1050～1150 DEG C, final forging temperature >=900 DEG C, after forging, air cooling is to room temperature.
Four, after strip plate is heated to 1100～1200 DEG C of insulation time enough, carries out rolling and become a useful person, be rolled into 55～80mm bars.Start rolling temperature is: 1050～1150 DEG C, finishing temperature >=900 DEG C, rolls rear air cooling to room temperature.
Five, bar Technology for Heating Processing is: solution treatment: 1l20～2 hours air coolings of 1140 DEG C of insulations.Ageing Treatment: 835～855 DEG C are incubated 24 hours, in 2 hours, stove is cooled to 20 hours air coolings of 695～715 DEG C of insulations.
Embodiment 7:
One, according to the formula dispensing in table 2, control C is 0.022%, Cr is 15.8%, Fe is 6.92%, Mn is 0.50%, Nb is 0.98%, Al is 0.81%, Ti is 2.61%, P is 0.006%, S is 0.002%, Si is 0.02%, Cu is 0.03%, Mg is 0.004%, Ce is 0.0034%, Zr is 0.043%, and surplus is nickel and inevitable impurity.
Two, by vacuum induction melting and be cast into Φ 290 electrode, electrode obtains Φ 400 steel ingot after argon shield electroslag or vacuum consumable remelting.Wherein remelting processing parameter sets, and such as molten speed etc., is limited occurring without metallurgical segregation in final steel ingot or finished product material.
Three, after Heating Steel Ingots is incubated at least 2h to 1100～1200 DEG C, carrying out hammer cogging, cogging is 120 side's strip plates.Opening forging temperature is: 1050～1150 DEG C, final forging temperature >=900 DEG C, after forging, air cooling is to room temperature.
Four, after strip plate is heated to 1100～1200 DEG C of insulation time enough, carries out rolling and become a useful person, be rolled into 55～80mm bars.Start rolling temperature is: 1050～1150 DEG C, finishing temperature >=900 DEG C, rolls rear air cooling to room temperature.
Five, bar Technology for Heating Processing is: solution treatment: 1l20～2 hours air coolings of 1140 DEG C of insulations.Ageing Treatment: 835～855 DEG C are incubated 24 hours, in 2 hours, stove is cooled to 20 hours air coolings of 695～715 DEG C of insulations.
Comparative example 1:
One, according to the formula dispensing in table 2, control C is 0.047%, Cr is 15.8%, Fe is 6.20%, Mn is 0.02%, Nb is 1.02%, Al is 0.85%, Ti is 2.50%, P is 0.005%, S is 0.005%, Si is 0.07%, Cu is 0.03%, and surplus is nickel and inevitable impurity.
Two, by vacuum induction melting and be cast into Φ 290 electrode, electrode obtains Φ 400 steel ingot after argon shield electroslag or consumable remelting.Wherein remelting processing parameter sets, and such as molten speed etc., is limited occurring without metallurgical segregation in final steel ingot or finished product material.
Three, after Heating Steel Ingots to 1100-1200 DEG C is incubated at least 2h, carrying out hammer cogging, cogging is 120 side's strip plates.Opening forging temperature is: 1050～1150 DEG C, final forging temperature >=900 DEG C, after forging, air cooling is to room temperature.
Four, after strip plate is heated to 1100-1200 DEG C of insulation time enough, carries out rolling and become a useful person, be rolled into 55-80mm bar.Start rolling temperature is: 1050～1150 DEG C, finishing temperature >=900 DEG C, rolls rear air cooling to room temperature.
Five, bar Technology for Heating Processing is: solution treatment: 2 hours air coolings of 1l30 DEG C ± 10 DEG C insulations.Ageing Treatment: 845 DEG C ± 10 DEG C are incubated 24 hours, in 2 hours, stove is cooled to 20 hours air coolings of 705 DEG C ± 10 DEG C insulations.
The chemical composition (percentage by weight) of the 2-in-1 gold of table
The mechanical property of the product of each embodiment and comparative example is as shown in table 3.
The mechanical property of table 3 alloy bar material
To sum up, after have employed technique scheme, the present invention has the advantages that: compared with existing X-750 alloy, have adjusted Al, the contents level of Mn element, reduce S, P impurity content, and logical Mg, Ce, the compound interpolation of Zr element, after using rational hot-working and Technology for Heating Processing, higher-strength and plasticity coupling can be obtained, substantially improve alloy middle temperature plasticity simultaneously, middle temperature rupture ductility stability contorting under 730 DEG C/345MPa is more than 8%, parts inefficacy in use can be substantially reduced, there is good application prospect.
Last it is noted that above example only in order to the present invention is described and and unrestricted technical scheme described in the invention；Therefore, although this specification with reference to each above-mentioned embodiment to present invention has been detailed description, but, it will be understood by those within the art that, still the present invention can be modified or equivalent；And all are without departing from the technical scheme of the spirit and scope of the present invention and improvement thereof, it all should be contained in scope of the presently claimed invention.
Claims (5)
1. a high-strength nickel based high-temperature alloy, it is characterised in that described alloy includes the following component of percentage: C:0.02～0.08%；Cr:14.0～17.0%；Fe:5.0～9.0%；Al:0.50～1.30%；Ti:2.25～2.75%；Nb:0.7～1.2%；Mn:0.02～1.0%；Mg:0.001～0.006%；Ce:0.001～0.03%；Zr:0.01～0.06%；S≤0.005%；P≤0.008%；Si≤0.30%；Cu≤0.30%, surplus is nickel and inevitable impurity.
2. the manufacture method of a high-strength nickel based high-temperature alloy as claimed in claim 1, it is characterized in that, smelting step is that vacuum induction smelting adds electroslag remelting or vacuum induction is smelted and added consumable remelting, and heat treatment step is that hammer cogging is become a useful person or Forge Heating rolls into material.
3. the manufacture method of high-strength nickel based high-temperature alloy as claimed in claim 2, it is characterised in that after the steel ingot obtained after described smelting is incubated at least 2h at 1100～1200 DEG C, carries out hammer cogging or is rolled into dish circle；Opening forging or start rolling temperature is: 1050～1150 DEG C, finish-forging or finishing temperature >=900 DEG C, after forging or roll rear air cooling to room temperature.
4. the manufacture method of high-strength nickel based high-temperature alloy as claimed in claim 2, it is characterized in that, described heat-treating methods includes solution treatment and Ageing Treatment, and wherein, described solution treatment is by the air cooling after 1120～1140 DEG C of insulations 2 hours of the rerolled steel after forging or after rolling；Described Ageing Treatment be the steel semi-finished product after solution treatment are incubated 24 hours at 835～855 DEG C after, after being cooled to 695～715 DEG C in 2 hours, be incubated 20 hours, air cooling.
5. the manufacture method of high-strength nickel based high-temperature alloy as claimed in claim 2, it is characterised in that described remelting processing parameter setting is limited to occur without metallurgical segregation in final steel ingot or finished product material.
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| CN108165831A (en) * | 2017-12-30 | 2018-06-15 | 无锡隆达金属材料有限公司 | A kind of high temperature alloy dummy block and preparation method thereof |
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| CN114457261A (en) * | 2020-11-10 | 2022-05-10 | 中国科学院上海应用物理研究所 | Corrosion-resistant nickel-based wrought superalloy for molten salt reactor and preparation method thereof |
| CN115233038A (en) * | 2022-06-23 | 2022-10-25 | 丹阳市金星镍材有限公司 | High-aluminum-content nickel-based high-temperature alloy and preparation method thereof |
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| CN115491545A (en) * | 2022-09-23 | 2022-12-20 | 中国联合重型燃气轮机技术有限公司 | Anti-oxidation long-life nickel-based high-temperature alloy and preparation method and application thereof |
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| CN108103359B (en) * | 2016-11-24 | 2020-11-20 | 宝武特种冶金有限公司 | High-molybdenum-nickel-based alloy sheet with width larger than or equal to 1000mm, manufacturing method and application |
| CN108103359A (en) * | 2016-11-24 | 2018-06-01 | 宝钢特钢有限公司 | High molybdenum nickel base alloy sheet, manufacturing method and the application of a kind of width >=1000mm |
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| CN115233038A (en) * | 2022-06-23 | 2022-10-25 | 丹阳市金星镍材有限公司 | High-aluminum-content nickel-based high-temperature alloy and preparation method thereof |
| CN115505860A (en) * | 2022-08-30 | 2022-12-23 | 河钢股份有限公司 | Production method of 55Ni20Cr10Fe9Co high-temperature alloy |
| CN115505860B (en) * | 2022-08-30 | 2023-12-29 | 河钢股份有限公司 | Production method of 55Ni20Cr10Fe9Co superalloy |
| CN115491545A (en) * | 2022-09-23 | 2022-12-20 | 中国联合重型燃气轮机技术有限公司 | Anti-oxidation long-life nickel-based high-temperature alloy and preparation method and application thereof |
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