CN106854741A - A kind of heat treatment method for recovering K417G alloy properties - Google Patents
A kind of heat treatment method for recovering K417G alloy properties Download PDFInfo
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- CN106854741A CN106854741A CN201610393977.3A CN201610393977A CN106854741A CN 106854741 A CN106854741 A CN 106854741A CN 201610393977 A CN201610393977 A CN 201610393977A CN 106854741 A CN106854741 A CN 106854741A
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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Abstract
The present invention relates to alloy material Field of Heat-treatment, specially a kind of heat treatment method for recovering K417G alloy properties, it is adaptable to which long-term use causes the K417G alloy materials of performance degradation to regain excellent properties.The method comprises the following steps：(1) heated up with stove or to warm shove charge, 0.1~2h is incubated at 1230~1250 DEG C；(2) with the cooling rate furnace cooling no less than 1 DEG C/min after insulation terminates；(3) 1~20h, air cooling are incubated at 750~900 DEG C.The present invention uses higher temperature solid solution first, the γ ' phases and M that will be roughened23C6Phase back dissolving；Again with appropriate cooling rate and the distribution of Ageing Treatment control crystal boundary and transgranular hardening constituent, to realize that alloy tensile and enduring quality recover again.So as to, by simple thermal treatment technique, the prolonged K417G casting of military service can be made to regain excellent performance, extend the service life of part.
Description
Technical field
The present invention relates to alloy material Field of Heat-treatment, at specially a kind of heat for recovering K417G alloy properties
Reason method, it is adaptable to which long-term use causes the K417G alloy materials of performance degradation to regain excellent properties.
Background technology
K417G alloys are a kind of γ ' (Ni high3(Al, Ti)) phase content ageing strengthening type nickel base cast high temperature close
Gold, with excellent combination property, mainly for the preparation of the hot-end component in aero-engine.Application at present
After part prepared by K417G alloys is mainly casting, no longer it is heat-treated, is directly used after processing.In height
After warm military service for a long time, there is roughening, crystal boundary wideization, carbide and decompose in the main hardening constituent γ ' in alloy, make
Gradually reduced into part performance.General part can only scrap treatment in use for some time, by new precision castings
Correlated parts are replaced, the maintenance cost of engine can be greatly increased.
Material for tissue breakdown is normalized, it is necessary to various roughening are organized into back dissolvings, in conjunction with
Appropriate Ageing Treatment is possible to realize the performance recovery of alloy to control the distribution of hardening constituent.Back dissolving
Be roughened tissue heat treatment temperature it is too low then cannot effective back dissolving, temperature is too high and easily causes severe oxidation, crystalline substance
The problems such as boundary liquefies.The complete cooldown rate of high-temperature process can not be too low, and γ ' can occur soon otherwise in cooling procedure
Speed roughening, causes intensity decreases.Alloy after high-temperature process needs in suitable temperature timeliness so that crystal boundary is separated out
Hardening constituent, the otherwise transgranular too high plasticity that easily causes of intensity is seriously reduced；Aging time is long, high cost,
Hold facility rate is high, is unfavorable for popularization and application.
The content of the invention
It is an object of the invention to provide the heat treatment that a kind of K417G alloy properties made after long-term use recover
Method, so as to improve part utilization rate.
The technical scheme is that：
A kind of heat treatment method for recovering K417G alloy properties, it is characterised in that comprise the following steps：
(1) heated up with stove or to warm shove charge, 0.1~2h is incubated at 1230~1250 DEG C；
(2) with the cooling rate furnace cooling no less than 1 DEG C/min after insulation terminates；
(3) 1~20h, air cooling are incubated at 750~900 DEG C.
The described heat treatment method for recovering K417G alloy properties, step (1) is higher temperature solid solution,
Step (3) is Ageing Treatment.
The described heat treatment method for recovering K417G alloy properties, after higher temperature solid solution, more than 1000 DEG C
Residence time is no more than 5h.
The described heat treatment method for recovering K417G alloy properties, in step (1), preferably at 1240 DEG C
0.25~1.5h of insulation.
The described heat treatment method for recovering K417G alloy properties, in step (2), furnace cooling it is cold
Speed is preferably 3~10 DEG C/min.
The described heat treatment method for recovering K417G alloy properties, in step (3), preferably 800~
900 DEG C of 5~16h of insulation.
Design philosophy of the invention is：
In order to set up the restoring heat treatment method of K417G alloy parts, the tissue according to alloy after long-term use declines
Become feature, it is necessary to back dissolving is roughened γ ' phases, and controls γ ' phase sizes and distribution, then profit by cooling rate and Ageing Treatment
Enough intercrystalline strengthening phases are separated out with Ageing Treatment, so as to improve combination property.
Wherein, higher temperature solid solution temperature will more than 1230 DEG C, otherwise cannot back dissolving roughening γ ' phases, temperature
It is too high, cause severe oxidation and internal liquid phase area to occur.More than 1000 DEG C residence times are no more than after solid solution
5h, otherwise γ ' phase sizes cross conference reduction intensity；Cooling rate can not be faster than air cooling, the otherwise boundary such as crystal boundary or eutectic
Face occurs obvious hardening flaw.In 750~900 DEG C of Ageing Treatments, if in 800~900 DEG C of soaking times
Can be shorter, if to be grown in 750 DEG C of times.
Advantages of the present invention and beneficial effect are：
1st, the K417G for tissue breakdown of the invention, first using higher temperature solid solution, the γ ' phases that will be roughened
And M23C6Phase back dissolving.Again with appropriate cooling rate and the distribution of Ageing Treatment control crystal boundary and transgranular hardening constituent,
To realize that alloy tensile and enduring quality recover again.
2nd, the present invention can regain the prolonged K417G casting of military service excellent by simple thermal treatment technique
Different performance, so as to extend the service life of part.
Brief description of the drawings
Fig. 1 is the typical organization of K417G cast alloy；
Fig. 2 is the tissue breakdown feature of K417G alloys after long-term use；
Fig. 3 is to be as cold as 800 DEG C of tissues of insulation 16h air cooling samples with 100min stoves after being incubated 1h at 1240 DEG C；
Fig. 4 is to be as cold as 850 DEG C of tissues of insulation 16h air cooling samples with 100min stoves after being incubated 1h at 1240 DEG C；
Fig. 5 is to be as cold as 900 DEG C of tissues of insulation 16h air cooling samples with 100min stoves after being incubated 1h at 1240 DEG C；
Fig. 6 is the tissue of water-cooled sample after being incubated 1h at 1220 DEG C；
Fig. 7 is the tissue of air cooling sample after being incubated 1h at 1220 DEG C with stove intensification；
Fig. 8 is to heat up be as cold as 900 DEG C of tissues of air cooling sample with 100min stoves after 1240 DEG C of insulation 1h with stove.
Specific embodiment
In specific implementation process, the present invention makes the heat treatment method that K417G alloy properties recover, concrete technology
Flow is：
(1) casting is heated up with stove or to warm shove charge, material is incubated 0.1~1h at 1230~1250 DEG C, filled
The M for dividing the γ ' of back dissolving roughening mutually and largely to separate out23C6Phase；If to part treatment, preferably in vacuum heat
Special tooling clamp retaining element is utilized in stove；
(2) after being incubated, (stove cool time does not surpass to be cooled to less than 1000 DEG C timeliness holding temperatures of coming out of the stove or be cooled to
3h is crossed, prevents the γ ' in cooling procedure from mutually growing up)；
(3) 1~20h is incubated at 750~900 DEG C, air cooling or stove are cold, so that alloy separates out crystal boundary M23C6Phase.
(4) cast properties use preceding level (900 DEG C of tensile properties close to casting：Rm >=637MPa, A >=6%,
Z >=6%；760 DEG C/645MPa enduring qualities：≥23h；950 DEG C/235MPa enduring qualities：≥40h).
Below, by comparative example and embodiment, the present invention is described in more detail.
Comparative example 1
K417G cast alloy and 900 DEG C of timeliness 5000h after-drawing and enduring quality are as shown in table 1.Compared to
Cast alloy, after 900 DEG C of timeliness 5000h, the tensile strength of K417G alloys is substantially reduced, plasticity
Improve；760 DEG C/645MPa creep rupture lives all substantially reduce, the requirement already below 23h；950℃/235MPa
Creep rupture life all substantially reduces, the technical requirements already below 40h.The as-cast structure of alloy as shown in figure 1,
It is main to include MC massive carbides, an a large amount of tiny γ ' mutually and γ ' phase eutectic compositions.900 DEG C of timeliness 5000h
Afterwards tissue as shown in Fig. 2 in alloy γ ' mutually substantially grow up, separated out around eutectic and MC carbide more
Block M23C6Phase, and along with more without the appearance for separating out area around.Group after 900 DEG C of timeliness 5000h
Knit the principal character for having reacted alloy structure decay, the material of follow-up study of the present invention be all tissue and performance
Through the sample of obvious decay.
Mechanical property after table 1, K417G alloy casting states and 900 DEG C of timeliness 5000h
Embodiment 1
In the present embodiment, the heat treatment method for recovering K417G alloy properties is as follows：
After being incubated 1h at 1240 DEG C, 800 DEG C are cooled to 100min, and be air cooled to after 800 DEG C of insulation 16h
Room temperature, the tissue of sample is as shown in Figure 3.It can be seen that, the γ ' phase amount of precipitations of alloy are larger, and size is relatively fine, brilliant
Also there is certain M at boundary23C6Mutually separate out.The performance test results are as shown in table 2,900 DEG C of tensile strengths of alloy,
760 DEG C and 950 DEG C of enduring qualities are significantly improved, and obtain excellent excellent combination property.
Table 2 is as cold as 800 DEG C of mechanical properties of insulation 16h air cooling samples after being incubated 1h at 1240 DEG C with 100min stoves
Embodiment 2
In the present embodiment, the heat treatment method for recovering K417G alloy properties is as follows：
After being incubated 1h at 1240 DEG C, 850 DEG C are cooled to 100min, and be air cooled to after 850 DEG C of insulation 16h
Room temperature, the tissue of sample is as shown in Figure 4.It can be seen that, the γ ' phase amount of precipitations of alloy are larger, and size is relatively fine, brilliant
Also there is certain M at boundary23C6Mutually separate out.The performance test results are as shown in table 3,900 DEG C of tensile strengths of alloy,
760 DEG C and 950 DEG C of enduring qualities are significantly improved, and obtain excellent excellent combination property.
Table 3 is as cold as 850 DEG C of mechanical properties of insulation 16h air cooling samples after being incubated 1h at 1240 DEG C with 100min stoves
Embodiment 3
In the present embodiment, the heat treatment method for recovering K417G alloy properties is as follows：
After being incubated 1h at 1240 DEG C, 900 DEG C are cooled to 100min, and be air cooled to after 900 DEG C of insulation 5h
Room temperature, the tissue of sample is as shown in Figure 5.It can be seen that, the γ ' phase amount of precipitations of alloy are larger, and size is relatively fine, brilliant
Also there is certain M at boundary23C6Mutually separate out.The performance test results are as shown in table 4,900 DEG C of tensile strengths of alloy,
760 DEG C and 950 DEG C of enduring qualities are significantly improved, and obtain excellent excellent combination property.
Table 4 is as cold as 90 DEG C of mechanical properties of insulation 16h air cooling samples after being incubated 1h at 1240 DEG C with 100min stoves
Comparative example 2
The tissue of sample water-cooled sample after 1240 DEG C of insulation 1h is as shown in Figure 6.It can be seen that, after solution treatment
Direct quenching is processed, and Precipitation γ ' phase amounts are less, and there is obvious hardening flaw in regions such as crystal boundaries,
It can be seen that cooling velocity can not be too high after solid solution.
Comparative example 3
Sample is as shown in Figure 7 with the tissue of stove intensification air cooling sample after 1220 DEG C of insulation 1h.It can be seen that, solid
Direct Air-Cooled after molten treatment, γ ' phase sizes are substantially coarser than cast alloy, or even to be coarser than 900 DEG C of timeliness 5000h thick
The tissue of change, illustrates the γ ' phases that the condition undertreatment is roughened with back dissolving, and solid solubility temperature is not enough.
Comparative example 4
Sample is heated up after being incubated 1h at 1240 DEG C with stove, and 900 DEG C of tissues of air cooling sample are as cold as with 100min stoves
As shown in Figure 8.It can be seen that, after solution treatment, the Ageing Treatment without certain hour and Direct Air-Cooled, γ ' phases
Although size is relatively thin, crystal boundary is almost without any precipitated phase.The performance of alloy is as shown in table 5 after the treatment,
It can be seen that 900 DEG C of stretching plastics of alloy and 760 DEG C/645MPa creep rupture lives are relatively low.
Table 5,1240 DEG C be incubated 1h after 900 DEG C of mechanical properties of air cooling are as cold as with 100min stoves
Embodiment result shows that the inventive method can make the K417G casting of performance degradation regain higher level
Stretching and enduring quality, so as to extend casting service life.
Claims (6)
1. it is a kind of to make the heat treatment method of K417G alloy properties recovery, it is characterised in that to comprise the following steps：
(1) heated up with stove or to warm shove charge, 0.1~2h is incubated at 1230~1250 DEG C；
(2) with the cooling rate furnace cooling no less than 1 DEG C/min after insulation terminates；
(3) 1~20h, air cooling are incubated at 750~900 DEG C.
2. as described in claim 1 make K417G alloy properties recover heat treatment method, it is characterised in that：
Step (1) is higher temperature solid solution, and step (3) is Ageing Treatment.
3. as described in claim 2 make K417G alloy properties recover heat treatment method, it is characterised in that：
After higher temperature solid solution, more than 1000 DEG C residence times are no more than 5h.
4. as described in claim 1 make K417G alloy properties recover heat treatment method, it is characterised in that：
In step (1), preferably 0.25~1.5h is incubated at 1240 DEG C.
5. as described in claim 1 make K417G alloy properties recover heat treatment method, it is characterised in that：
In step (2), the cooling rate of furnace cooling is preferably 3~10 DEG C/min.
6. as described in claim 1 make K417G alloy properties recover heat treatment method, it is characterised in that：
In step (3), preferably 5~16h is incubated at 800~900 DEG C.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110284087A (en) * | 2019-05-23 | 2019-09-27 | 中国人民解放军第五七一九工厂 | A kind of restoring heat treatment method for repairing K403 nickel base superalloy blade creep impairment |
| CN114309657A (en) * | 2021-12-28 | 2022-04-12 | 北京钢研高纳科技股份有限公司 | Heat treatment method of SLM (selective laser melting) formed GH3536 high-temperature alloy material and application thereof |
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| CN101089215A (en) * | 2006-06-16 | 2007-12-19 | 中国科学院金属研究所 | High strength antithermal corrosion low segregation directional high temp alloy |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN110284087A (en) * | 2019-05-23 | 2019-09-27 | 中国人民解放军第五七一九工厂 | A kind of restoring heat treatment method for repairing K403 nickel base superalloy blade creep impairment |
| CN114309657A (en) * | 2021-12-28 | 2022-04-12 | 北京钢研高纳科技股份有限公司 | Heat treatment method of SLM (selective laser melting) formed GH3536 high-temperature alloy material and application thereof |
| CN114309657B (en) * | 2021-12-28 | 2023-08-15 | 北京钢研高纳科技股份有限公司 | Heat treatment method and application of GH3536 high-temperature alloy material formed by SLM (selective laser melting) |
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