CN101538664A - Nickel-base high-temperature alloy with low density and high melting point and preparation process thereof - Google Patents
Nickel-base high-temperature alloy with low density and high melting point and preparation process thereof Download PDFInfo
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- CN101538664A CN101538664A CN200810010697A CN200810010697A CN101538664A CN 101538664 A CN101538664 A CN 101538664A CN 200810010697 A CN200810010697 A CN 200810010697A CN 200810010697 A CN200810010697 A CN 200810010697A CN 101538664 A CN101538664 A CN 101538664A
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- 239000000956 alloy Substances 0.000 title claims abstract description 138
- 238000002360 preparation method Methods 0.000 title claims abstract description 14
- 238000002844 melting Methods 0.000 title abstract description 19
- 230000008018 melting Effects 0.000 title abstract description 19
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 68
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 28
- 239000011651 chromium Substances 0.000 claims abstract description 20
- 238000005516 engineering process Methods 0.000 claims abstract description 17
- 238000005266 casting Methods 0.000 claims abstract description 16
- 239000010955 niobium Substances 0.000 claims abstract description 15
- 229910017052 cobalt Inorganic materials 0.000 claims abstract description 14
- 239000010941 cobalt Substances 0.000 claims abstract description 14
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims abstract description 14
- 230000006698 induction Effects 0.000 claims abstract description 14
- 238000003756 stirring Methods 0.000 claims abstract description 12
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 11
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 11
- 238000007670 refining Methods 0.000 claims abstract description 11
- 238000005275 alloying Methods 0.000 claims abstract description 10
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 10
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 9
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 9
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 9
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 8
- 241001062472 Stokellia anisodon Species 0.000 claims abstract description 8
- 239000011733 molybdenum Substances 0.000 claims abstract description 8
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims abstract description 8
- 239000010937 tungsten Substances 0.000 claims abstract description 8
- 238000003723 Smelting Methods 0.000 claims abstract description 7
- 238000000034 method Methods 0.000 claims abstract description 7
- 229910018138 Al-Y Inorganic materials 0.000 claims abstract description 6
- 239000000203 mixture Substances 0.000 claims abstract description 5
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- 238000009415 formwork Methods 0.000 claims description 8
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- 229910001257 Nb alloy Inorganic materials 0.000 claims description 5
- 210000000795 conjunctiva Anatomy 0.000 claims description 5
- 239000000463 material Substances 0.000 abstract description 6
- 229910052758 niobium Inorganic materials 0.000 abstract description 5
- 229910052796 boron Inorganic materials 0.000 abstract description 3
- 238000002485 combustion reaction Methods 0.000 abstract description 3
- 238000007667 floating Methods 0.000 abstract description 3
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 abstract description 3
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- 238000005520 cutting process Methods 0.000 abstract 1
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- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
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- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 description 2
- 239000004411 aluminium Substances 0.000 description 1
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- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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Abstract
The invention relates to high-temperature alloy technology, and in particular provides an isometrical cast nickel-base high-temperature alloy with low density, high incipient melting temperature and good casting property and a preparation process thereof, which can be used for floating tile materials of a combustion chamber. The alloy comprises the following compositions by mass percentage: 0.03 to 0.06 percent of C, 5 to 12 percent of Cr, 5.5 to 6.5 percent of Al, 3 to 8 percent of Co, 3 to 7 percent of W, 2 to 4 percent of Mo, 1.6 to 3.2 percent of Nb, 0.01 to 0.03 percent of B, 0.008 to 0.025 percent of Y and the balance of Ni. A vacuum induction furnace is adopted to smelt a master alloy, and a smelting crucible is a CaO crucible or a MgO crucible; and the operation process comprises the following steps: putting alloying elements such as carbon, chromium, cobalt, tungsten, molybdenum and niobium in proportion and a nickel plate into the crucible; melting the alloy when the vacuum degree reaches between 50 and 0.1 Pa; and after completion of the melting, refining for 30 to 300 seconds at a temperature of between 1,550 and 1,600 DEG C, cutting off electricity, forming a film, breaking the film to add Al and Al-Y and Ni-B interalloy for uniform stirring, and casting a master alloy pig at a temperature of between 1,450 and 1,500 DEG C. The invention solves the problems of low incipient melting temperature, poor plasticity and inoxidability and the like of the nickel-base high-temperature alloy.
Description
Technical field
The present invention relates to the superalloy technology, provide especially a kind of low density, high initial melting temperature have good castability etc. axle cast nickel-base alloy and preparation technology thereof, can be used for combustion chamber flame tube floating tile material.
Background technology
Superalloy is meant that with iron, nickel, cobalt be base, a metalloid material that can long term operation under the high temperature more than 600 ℃ and certain stress.Since half a century, temperature is brought up to 1677 ℃ from 730 ℃ of the forties before the aero-turbine.The raising of use temperature has proposed more and more harsher requirement to materials for aeroengines.Nickel base superalloy is that performance is the most superior so far, and purposes is materials for aeroengines the most extensively.The ceiling temperature of current this alloy use temperature has reached about 1200 ℃, has approached the fusing point of alloy, but still is that withstand temp is the highest in the present advanced engine, the preferred material of the key part of stress-loaded maximum.
Nickel base superalloy has the excellent resistance to high temperature oxidation and the performance of high temperature corrosion.Compare with iron-base superalloy, nickel base superalloy has good thermal conductivity, higher structure stability, can the more element of solid solution and do not produce harmful phase; Nickel base superalloy is compared with cobalt base alloy, has light specific gravity, price is low, intensity is high and the characteristics of good in oxidation resistance.In addition, nickel base superalloy also has good castability and high temperature endurance performance.
That determine the nickel base superalloy excellent properties is face-centered cubic intermetallic compound γ ' phase (Ni that its precipitation is separated out
3Al) strengthen.Also orderly body-centered teteragonal the γ " (Ni of some alloy such as In718
3Nb) strengthen.General cobalt base superalloy only depends on solution strengthening and carbide reinforced owing to lack the strengthening effect of γ ' phase, therefore generally is difficult to reach the strength level of nickel base superalloy.
Nickel base superalloy is by suitably regulating alloying constituent, can make alloy not only have the incomparable hot strength of cobalt base alloy, but also has higher initial melting temperature, cold and hot fatigue property, higher plasticity and toughness preferably, higher anti-oxidant and erosion resistance, lower density, application has special meaning on a lot of parts of aircraft engine.
Although the domestic nickel base superalloy that is used for aircraft engine has been developed much, alloys such as K403, K405, K441 and K417G for example, the shortcoming of these alloy maximums is exactly that initial melting temperature and plasticity are compared with cobalt base superalloy and differed bigger, has limited the application of these alloys.In addition, because the combustion chamber flame tube floating tile is complex-shaped, is not easy to be prepared into monocrystalline or adopts directional solidification processes.Though intermetallic compound has the low and advantages of high strength of proportion,, limited its use because its plasticity and oxidation-resistance are relatively poor.So just need a kind of alloy of exploitation, require to have high initial melting temperature, low density, have good castability, good thermal fatigue property and higher high temperature oxidation resistance.
Summary of the invention
The object of the present invention is to provide the over-all properties of a kind of high initial melting temperature, good hot strength, low-gravity and lower cost, good castability superior etc. axle cast nickel-base alloy and preparation technology thereof, it is lower to solve the nickel base superalloy initial melting temperature, and problem such as plasticity and oxidation-resistance be relatively poor.
Technical scheme of the present invention is:
A kind of low density high-melting-point nickel base superalloy, by mass percentage, alloying constituent is as follows:
C 0.03～0.06, and Cr 5～12, and Al 5.5～6.5, and Co 3～8, and W 3～7, and Mo 2～4, and Nb 1.6～3.2, and B 0.01～0.03, and Y 0.008～0.025, the Ni surplus.
The preparation technology of this alloy is:
Adopt the vacuum induction furnace smelting mother alloy, smelt crucible and select CaO or MgO crucible for use, operating process is: by described component carbon, chromium, cobalt, tungsten, molybdenum, niobium alloy element and nickel plate are packed in the crucible; Vacuumize also small power heating to get rid of gas.When vacuum tightness reaches 50Pa～0.1Pa, give high-power melted alloy; After fusing finished, at 1550 ℃～1600 ℃ refining 30s～300s, vacuum tightness should reach 0.1Pa～0.001Pa, and power failure, conjunctiva, rupture of membranes add Al and Al-Y and Ni-B master alloy, evenly stir, and are cast into master alloy ingot at 1450 ℃～1500 ℃.
When described nickel base superalloy casting coupon or foundry goods, with casting behind the vacuum induction furnace remelting master alloy ingot, the formwork of casting is at 850 ℃～1100 ℃ preheating 3～5h; Concrete technology is: required master alloy ingot is put into CaO or MgO crucible, get rid of gas for electricity; When vacuum tightness reaches 50Pa～0.01Pa level, add high-power melted alloy; At 1550 ℃～1600 ℃ refining 30S～300S, vacuum tightness should reach 0.1Pa～0.001Pa, casts in the time of 1450 ℃～1500 ℃; Cast, in vacuum chamber, cooled off, waited and solidify the back taking-up fully.
Temp measuring system of the present invention is W-Re galvanic couple and JH-5 type infrared ray optical direction temperature/vacuum degree measuring instrument, and the thermometric protective casing is Mo-Al
2O
3Metal ceramic tube.
Described superalloy, by mass percentage, composition is as follows preferably:
C 0.05, and Cr 9, and Al 6, and Co 5.5, and W 3.5, and Mo 3, and Nb 2.2, and B 0.023, and Y 0.013, the Ni surplus.
Described superalloy, different on request, can take different heat treating regimes, obtain the performance that requirement reaches:
Heat treating regime one:
Under 1090 ℃～1110 ℃, insulation 3h～5h, air cooling is to room temperature.
This heat treating regime can obtain plasticity preferably, has taken into account intensity.
Heat treating regime two:
Under 1200 ℃～1220 ℃, insulation 3h～5h, air cooling is to room temperature;
Under 1040 ℃～1060 ℃, insulation 3h～5h, air cooling is to room temperature;
Under 850 ℃～890 ℃, insulation 20h～28h, air cooling is to room temperature.
This heat treating regime can obtain tensile strength and creep property preferably.
Principle of work of the present invention is as follows:
In superalloy, Al and Ti are topmost γ ' forming elements.The present invention mainly is that the γ ' that adds more aluminium formation high-volume fractional improves its intensity mutually; Because Ti sharply reduces the temperature of fusion of alloy, so complete restricted T i in this alloy.Further increase γ ' phase amount by adding niobium, improved the lattice misfit degree of γ-γ ', strengthened the strengthening effect of γ ' phase, and formed stable MC with carbon; Add a spot of carbon and boron, strengthen crystal boundary on the one hand, come reinforced alloys with chromium, tungsten, molybdenum, niobium formation carbide and boride on the other hand; Alloying element solid solution strengthened alloys such as chromium, tungsten, molybdenum.The content of alloy carbon and boron is lower, and titaniferous has not guaranteed this alloy initial melting temperature height, and cold and hot fatigue property is good; Chromium and yttrium can improve resistance of oxidation; Yttrium can also improve carbide morphology, improves its stability and cracking resistance ability; The effect of cobalt is solution strengthening, can replace with Ni.Alloy sample of the present invention adopts current in the world conventional cast technology preparation, and good casting property is easy to processing.
The alloy of this invention has following advantage:
1, alloy initial melting temperature height.The high temperature dsc analysis shows: alloy initial melting temperature of the present invention is higher than K419, K417G, K418 and K441 superalloy and reaches 90 ℃, 70 ℃, 50 ℃ 30 ℃ respectively, also a little more than cobalt base alloys such as DZ40M, K640 up to 1347 ℃.
2, good casting property.1347 ℃～1375 ℃ of the temperature of fusion scopes of alloy of the present invention, the freezing range is little, can water to cast out complex-shaped parts.
3, alloy density is lower.Alloy density of the present invention only is 8.1g/cm
3, far below alloys such as K441, K640.
4, the alloy antioxidant property is good.1100 ℃ of oxidation weight gain speed of alloy of the present invention are 0.067g/m
2H, and in 900 ℃～1100 ℃ temperature ranges, all reach complete anti-oxidant level.
5, cold and hot fatigue property is good.Alloy crack growth rate of the present invention is only far below alloys such as K465, K417G, DZ40M.
6, the phase stability of alloy of the present invention is good, and long-term timeliness also is difficult for generating harmful phase.
7, cost is low.Alloy of the present invention does not contain noble elements such as tantalum, hafnium, and price is far below DZ40M and K640 alloy.
8, intensity height.On all temperature, alloy of the present invention stretches and all close far above initial melting temperature DZ40M and the K640 alloy of creep rupture strength.
Description of drawings
Fig. 1 (a)-Fig. 1 (c) is an alloy organizing form of the present invention.Wherein, the typical cast alloy tissue of Fig. 1 (a); Strengthening phase γ ' the form of Fig. 1 (b) cast alloy; γ ' form after 1100 ℃ of thermal treatments in 4 hours of Fig. 1 (c).
Fig. 2 is the oxidation weight gain curve of this alloy.
Fig. 3 is the thermal fatigue property curve of this alloy.
Fig. 4 (a)-Fig. 4 (b) is this alloy at the fatigue curve of 700 ℃ and 900 ℃.Wherein, Fig. 4 (a) is 700 ℃ a fatigue curve, and Fig. 4 (b) is 900 ℃ a fatigue curve.
Embodiment
Below by example in detail the present invention is described in detail.
Embodiment 1
The present embodiment composition sees Table 1:
Table 1 alloying constituent table of the present invention (wt.%)
| C | Cr | Co | Al | W | Mo | Nb | Y | B | Ni | |
| Embodiment 1 | 0.045 | 9.0 | 5.0 | 5.9 | 3.5 | 3.0 | 2.3 | 0.013 | 0.023 | Surplus |
The preparation technology of this alloy is: adopt vacuum induction furnace smelting experiment mother alloy, smelt crucible and select the CaO crucible for use, temp measuring system is W-Re galvanic couple and JH-5 type infrared ray optical direction temperature/vacuum degree measuring instrument, and the thermometric protective casing is Mo-Al
2O
3Metal ceramic tube.To smelt the 300kg mother alloy, operating process is: carbon, chromium, cobalt, tungsten, molybdenum, niobium alloy element and nickel plate are packed in the crucible; Vacuumize, get rid of for small power 130kw baking crucible and adhere to gas, when vacuum tightness reaches 20Pa, add high-power to the 200kw melted alloy; After fusing finishes, 1580 ℃ of refining 4min (vacuum tightness is 0.06Pa, and power is 90kw).Power failure, conjunctiva, rupture of membranes add Al and Al-Y and Ni-B master alloy, and 130kw stirs then, stir back power failure cooling, and 90kw impacts rupture of membranes, is cast into master alloy ingot at 1480 ℃.
Behind the remelting mother alloy, cast alloy coupon adopts the CaO crucible in testing with the 10kg vacuum induction furnace, and temp measuring system is the W-Re galvanic couple.Casting cycle is: MgO or CaO formwork are imbedded SiO is housed
2In the sand tube, the 900 ℃ of preheatings 3 hours in retort furnace in advance of the formwork of casting.Required master alloy ingot is put into the CaO crucible, the sand wound packages that just goes out retort furnace is gone into to wait in the vacuum induction furnace to cast.Vacuumize, get rid of gas for small power 10kw, when vacuum tightness reaches the 5Pa level, increase power again to the 40kw melted alloy, and at 1550 ℃ of refining 30S (vacuum tightness is to 0.05Pa, and power is 10kw).The cooling that has a power failure is waited to cast, and adds high-powerly to 20kw, heats up and stirs, and regulates the power controlled temperature, and pouring temperature should be at about 1470 ℃.Cast, in vacuum chamber, cooled off, waited and solidify the back taking-up fully.Alloy typical case cast alloy tissue of the present invention is seen Fig. 1 (a), and the strengthening phase γ ' form of cast alloy is seen Fig. 1 (b).
Alloy initial melting temperature of the present invention is higher than nickel base superalloys such as K419, K417G, K418 and K441 and reaches 90 ℃, 70 ℃, 50 ℃, 30 ℃ respectively up to 1352 ℃, also is higher than cobalt base superalloys (seeing Table 2) such as DZ40M, K640 alloy.The freezing range is little, and castability is superior.Alloy density is low, only is 8.1g/cm
3, far below DZ40M, K640 alloy (seeing Table 3).Invention alloy antioxidant property is good, and 1100 ℃ of oxidation weight gain speed are 0.067g/m
2H reaches complete anti-oxidant level, sees Fig. 2.The cold and hot fatigue property of alloy of the present invention (K495) is good, and crack growth rate is seen Fig. 3 far below alloys such as K465, K417G, DZ40M.Strength ratio is higher, and on 20 ℃ and 1000 ℃ of two representative temperatures, the alloy tensile strength is in medium in the several typical cast superalloys of table 4, and plasticity only is lower than the DZ40M alloy.Its initial melting temperature of alloy that strength ratio invention alloy is high in the table 4 is far below this invention alloy.Alloy creep rupture strength of the present invention still is all to be higher than DZ40M and K640 creep rupture life, and this invention alloy also is very outstanding in table 5.Illustrate that alloy of the present invention is the superior conventional cast superalloy of over-all properties.
The temperature of fusion scope of some cast superalloys of table 2
| Alloy | The temperature of fusion scope (℃) |
| Alloy of the present invention | 1347～1375 |
| K403 | 1260～1338 |
| K419 | 1260～1340 |
| K418 | 1295～1345 |
| K417G | 1281～1327 |
| K441 | 1320～1410 |
| K640 | 1340～1396 |
| DZ40M | 1345～1395 |
The density of some cast superalloys of table 3
| Alloy | Density p (10 3kg/m 3) |
| Alloy of the present invention | 8.10 |
| K403 | 8.10 |
| K405 | 8.12 |
| K417L | 7.80 |
| K441 | 8.8 |
| K640 | 8.68 |
| DZ40M | 8.68 |
The tensile property of some cast superalloys of table 4
Among the present invention, UTS is a tensile strength, and 0.2YS is a yield strength, and δ is a unit elongation, and ψ is a relative reduction in area.
The creep rupture life of some cast superalloys of table 5
| Numbering | θ/℃ | Permanent stress/MPa | Creep rupture life/h |
| Alloy of the present invention | 980 | 120 | ＞100 |
| K418B | 980 | 150 | ≥50 |
| K417L | 980 | 120 | ≥18 |
| K441 | 980 | 83 | ≥18 |
| K640 | 982 | 55 | ≥100 |
| DZ40M | 980 | 83 | 71.4 |
Embodiment 2
Difference from Example 1 is that the alloying constituent of present embodiment is shown in Table 6:
Table 6 tested alloys component list (wt.%)
| C | Cr | Co | Al | W | Mo | Nb | Y | B | Ni | |
| Embodiment 2 | 0.05 | 9.0 | 5.0 | 5.9 | 3.4 | 3.0 | 2.2 | 0.015 | 0.021 | Surplus |
The preparation technology of this alloy is: adopt vacuum induction furnace smelting experiment mother alloy, smelt crucible and select the CaO crucible for use, temp measuring system is W-Re galvanic couple and JH-5 type infrared ray optical direction temperature/vacuum degree measuring instrument, and the thermometric protective casing is Mo-Al
2O
3Metal ceramic tube.Smelt 200kg mother alloy meter, its operating process is: carbon, chromium, cobalt, tungsten, molybdenum, niobium alloy element and nickel plate are packed in the crucible; Vacuumize, get rid of for power 120kw baking crucible and adhere to gas, when vacuum tightness reaches 1Pa, increase power to the 180kw melted alloy; After fusing finishes, at 1550 ℃ of refining 4min (vacuum tightness 0.08Pa, power 80kw), power failure, conjunctiva, rupture of membranes add Al and Al-Y and Ni-B master alloy, and high-power then 120kw stirs, and stir back power failure cooling, high-power 120kw impacts rupture of membranes, thermometric is adjusted power, is cast into master alloy ingot at 1450 ℃.
Behind the remelting mother alloy, cast alloy coupon adopts the CaO crucible in testing with the 10kg vacuum induction furnace, and temp measuring system is the W-Re galvanic couple.Casting cycle is: MgO or CaO formwork are imbedded SiO is housed
2In the sand tube, the 1000 ℃ of preheatings 4 hours in retort furnace in advance of the formwork of casting.Required master alloy ingot is put into the CaO crucible, and the sand wound packages that will just go out retort furnace again goes into to wait in the vacuum induction furnace to cast.Vacuumize, get rid of gas for 10kw power, when vacuum tightness reaches the 1Pa level, increase power 40kw melted alloy, and (vacuum tightness is 3 * 10 at 1550 ℃ of refining 4min
-2Pa, small power 10kw insulation).The cooling that has a power failure is waited to cast, and adds high-powerly to 20kw, heats up and stirs, and regulates the power controlled temperature, and pouring temperature is at 1450 ℃.Cast, in vacuum chamber, cooled off, waited and solidify the back taking-up fully.Present embodiment alloy initial melting temperature is up to 1347 ℃.
Watering the sample that casts out after heat treatment compares with DZ40M, K418B, K441, K640 etc.
Heat treating regime is: under 1100 ℃, and insulation 4h, air cooling is to room temperature, and the γ ' form of alloy is seen Fig. 1 (c) after the thermal treatment.
Table 7 is contrasts of creep rupture test result.Table 8 is contrasts of this routine breach enduring quality, shows that this alloy does not have notch sensitivity substantially.Table 9 is these routine tensile properties.Fig. 4 (a)-Fig. 4 (b) is 700 ℃ and 900 ℃ of low cycle fatigue properties, and the K495 alloy is alloy of the present invention among the figure.
Some alloy 100h left and right sides creep rupture strengths (MPa) of table 7
| Temperature/℃ | Alloy of the present invention | DZ40M | K418B | K441 | K640 |
| 700 | 600 | 400 | 690 | - | 380 |
| 800 | 500 | 265 | 485 | 341 | 240 |
| 850 | 350 | 185 | 245 | 251 | 185 |
| 900 | 250 | 140 | 240 | 169 | 125 |
| 980 | 120 | 83 | - | 80 | - |
Table 8 tested alloys breach enduring quality
| Temperature/℃ | Stress/MPa | Smooth sample | Notched specimen |
| 700 | 680 | 100 | 1008 |
| 850 | 400 | 88 | 964 |
| 980 | 151 | 68 | 254 |
| 1040 | 80 | 63 | 313 |
The tensile property of table 9 tested alloys
| θ/℃ | UTS(MPa) | 0.2YS(MPa) | δ(％) | ψ(％) |
| 20 | 852 | 758 | 10.2 | 17.2 |
| 1000 | 438 | 328 | 23 | 31.5 |
Embodiment 3
The alloying constituent of embodiment is as follows:
Table 10 tested alloys component list (wt.%)
| C | Cr | Co | Al | W | Mo | Nb | Y | B | Ni | |
| Embodiment 3 | 0.055 | 9.0 | 5.0 | 5.9 | 5.9 | 3.0 | 2.3 | 0.017 | 0.021 | Surplus |
The preparation technology of this alloy is: adopt vacuum induction furnace smelting experiment mother alloy, smelt crucible and select the CaO crucible for use, temp measuring system is W-Re galvanic couple and JH-5 type infrared ray optical direction temperature/vacuum degree measuring instrument, and the thermometric protective casing is Mo-Al
2O
3Metal ceramic tube.The mother alloy quantity of smelting is 20kg, and operating process is: carbon, chromium, cobalt, tungsten, molybdenum, niobium alloy element and nickel plate are packed in the crucible; Vacuumize, get rid of for small power 30kw baking crucible and adhere to gas, when vacuum tightness reaches 0.1Pa, increase power to the 60kw melted alloy; After fusing finishes, at 1600 ℃ of refining 2min (vacuum tightness 0.03Pa, power is 20kw), power failure, conjunctiva, rupture of membranes add Al and Al-Y and Ni-B master alloy, high-power then 70kw stirs, and stirs back power failure cooling, and high-power 70kw impacts rupture of membranes, thermometric is also regulated power to 1500 ℃, is cast into master alloy ingot.
Behind the remelting mother alloy, cast alloy coupon adopts the CaO crucible in testing with the 10kg vacuum induction furnace, and temp measuring system is the W-Re galvanic couple.Casting cycle is: MgO or CaO formwork are imbedded SiO is housed
2In the sand tube, the 900 ℃ of preheatings 3 hours in retort furnace in advance of the formwork of casting.Required master alloy ingot is put into the CaO crucible, and the sand wound packages that will just go out retort furnace again goes into to wait in the vacuum induction furnace to cast.Get rid of gas for small power 10kw, when vacuum tightness reaches the 10Pa level, increase power to the 40kw melted alloy, and at 1550 ℃ of refining 240s (vacuum tightness 0.03Pa, power 10kw).The cooling that has a power failure is waited to cast, and adds high-powerly to 20kw, heats up and stirs, and regulates the power controlled temperature, and pouring temperature is at 1470 ℃.Cast, in vacuum chamber, cooled off, waited and solidify the back taking-up fully.Present embodiment alloy initial melting temperature is up to 1351 ℃.
The main difference of alloying constituent that this is routine and precedent is content and the heat treating regime of W.The content of W (mass percent) brings up to 5.9%, and the heat treating regime system is selected following three grades of heat treating regimes simultaneously:
Under 1215 ℃, insulation 4h, air cooling is to room temperature;
Under 1050 ℃, insulation 4h, air cooling is to room temperature;
Under 870 ℃, insulation 24h, air cooling is to room temperature.
Table 11 is listed the tensile property of this test, and table 12 is enduring qualities of this tested alloys.Show by above-mentioned composition and heat treating regime, can further improve the hot strength of this alloy.
The tensile property of table 11 tested alloys
| θ/℃ | UTS(MPa) | 0.2YS(MPa) | δ(％) | ψ(％) |
| 20 | 1013 | 848 | 11 | 15.8 |
| 900 | 745 | 542.5 | 11.8 | 34 |
| 1000 | 488 | 340 | 17 | 37 |
| 1100 | 260 | 180 | 18.5 | 34.5 |
The enduring quality of table 12 tested alloys
Embodiment 4-6
Difference from Example 1 is: the Cr of embodiment 4 and Nb content obviously improve, and some decline of the content of C and W; The Co of embodiment 5 and Mo improve, and Cr and Nb then have decline; Some raising of W content of embodiment 6, other elements constant substantially (seeing Table 13).
Table 13 alloying constituent table of the present invention (wt.%)
| C | Cr | Co | Al | W | Mo | Nb | Y | | Ni | |
| Embodiment | ||||||||||
| 4 | 0.03 | 12.0 | 5.0 | 5.5 | 3.0 | 2.5 | 3.0 | 0.020 | 0.027 | Surplus |
| Embodiment 5 | 0.06 | 5.0 | 8.0 | 6.5 | 3.5 | 4.0 | 1.6 | 0.025 | 0.015 | Surplus |
| Embodiment 6 | 0.05 | 9.0 | 5.5 | 6.0 | 5 | 3.0 | 2.2 | 0.013 | 0.023 | Surplus |
The temperature of fusion of above-mentioned alloy is in 1347 ℃～1375 ℃ scopes.
Above-mentioned heat treatment of alloy system is as follows:
Under embodiment 4:1110 ℃, insulation 5h, air cooling is to room temperature.
Under embodiment 5:1210 ℃, insulation 4h, air cooling is to room temperature; Under 1040 ℃, insulation 4h, air cooling is to room temperature; Under 850 ℃, insulation 28h, air cooling is to room temperature.
Under embodiment 6:1220 ℃, insulation 3h, air cooling is to room temperature; Under 1060 ℃, insulation 3h, air cooling is to room temperature; Under 890 ℃, insulation 20h, air cooling is to room temperature.
The tensile property of the above-mentioned alloy of table 14
Claims (6)
1, a kind of low density high-melting-point nickel base superalloy is characterized in that by mass percentage, alloying constituent is as follows:
C 0.03～0.06, and Cr 5～12, and Al 5.5～6.5, and Co 3～8, and W 3～7, and Mo 2～4, and Nb 1.6～3.2, and B 0.01～0.03, and Y 0.008～0.025, the Ni surplus.
According to the described nickel base superalloy of claim 1, it is characterized in that 2, by mass percentage, composition is as follows preferably:
C 0.05, and Cr 9, and Al 6, and Co 5.5, and W 3.5, and Mo 3, and Nb 2.2, and B 0.023, and Y 0.013, the Ni surplus.
3, according to the preparation technology of the described nickel base superalloy of claim 1, it is characterized in that, adopt the vacuum induction furnace smelting mother alloy, smelt crucible and select CaO or MgO crucible for use, operating process is: by described component carbon, chromium, cobalt, tungsten, molybdenum, niobium alloy element and nickel plate are packed in the crucible; When vacuum tightness reaches 50Pa～0.1Pa, melted alloy; After fusing finished, at 1550 ℃～1600 ℃ refining 30s～300s, vacuum tightness should reach 0.1Pa～0.001Pa, and power failure, conjunctiva, rupture of membranes add Al and Al-Y and Ni-B master alloy, evenly stir, and are cast into master alloy ingot at 1450 ℃～1500 ℃.
According to the preparation technology of the described nickel base superalloy of claim 3, it is characterized in that 4, when described nickel base superalloy casting coupon or foundry goods, with casting behind the vacuum induction furnace remelting master alloy ingot, the formwork of casting is at 850 ℃～1100 ℃ preheating 3～5h; Concrete technology is: required master alloy ingot is put into CaO or MgO crucible, get rid of gas for electricity; When vacuum tightness reaches 50Pa～0.01Pa level, melted alloy; At 1550 ℃～1600 ℃ refining 30S～300S, vacuum tightness should reach 0.1Pa～0.001Pa, casts in the time of 1450 ℃～1500 ℃; Cast, in vacuum chamber, cooled off, waited and solidify the back taking-up fully.
According to the preparation technology of claim 3 or 4 described nickel base superalloys, it is characterized in that 5, the alloy heat treating regime is: under 1090 ℃～1110 ℃, insulation 3h～5h, air cooling is to room temperature.
According to the preparation technology of claim 3 or 4 described nickel base superalloys, it is characterized in that 6, the alloy heat treating regime is:
Under (1) 1200 ℃～1220 ℃, insulation 3h～5h, air cooling is to room temperature;
Under (2) 1040 ℃～1060 ℃, insulation 3h～5h, air cooling is to room temperature;
Under (3) 850 ℃～890 ℃, insulation 20h～28h, air cooling is to room temperature.
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