CN103361585A - Homogenization treatment process of high-alloying GH742 high temperature alloy - Google Patents
Homogenization treatment process of high-alloying GH742 high temperature alloy Download PDFInfo
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- CN103361585A CN103361585A CN2012100980392A CN201210098039A CN103361585A CN 103361585 A CN103361585 A CN 103361585A CN 2012100980392 A CN2012100980392 A CN 2012100980392A CN 201210098039 A CN201210098039 A CN 201210098039A CN 103361585 A CN103361585 A CN 103361585A
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Abstract
The invention relates to a homogenization treatment process of a high-alloying GH742 high temperature alloy. The process comprises the following steps of: heating a GH742 alloy ingot along with a furnace to 1050-1110 DEG C, wherein the average heating rate is 200-400 DEG C/h, and insulating for 20-60 hours; then, heating the furnace temperature to 1160-1200 DEG C, wherein the average heating rate is 2-10 DEG C/min, and insulating for 20-60 hours; and finally, cooling the treated ingot to below 500 DEG C, and taking out to air cool to room temperature; and after grinding the surface of the cooled ingot on the surface, and subsequently casting and cogging on a forging hammer. The process adopts two homogenization steps of low temperature pretreatment and high temperature diffusion to improve the heat processing plasticity of the GH742 alloy ingot and reduce the resistance to deformation, so that the forged blank obtains uniform and complete recrystallization textures.
Description
Technical field
The invention belongs to high-alloying superalloy ingot casting field, a kind of homogenizing treatment process of high-alloying GH742 superalloy is provided especially.
Background technology
The GH742 alloy is a kind of typical high-alloying ni-base wrought superalloy with excellent high-temperature behavior, be widely used as the key parts such as the gas-turbine unit turbine dish of working below 800 ℃ and compressor disc, in high-performance enginer, bringing into play very important effect.The alloying level of GH742 alloy is very high, and element segregation is very serious, and in a large number (γ+γ ') eutectic, Laves phase, σ phase, δ phase and Ni are separated out in the interdendritic
5Ce equates harmful fragility phase, a MC type carbide size of separating out in the process of setting is larger, assemble distribution in the interdendritic, cause its hot-work problem very outstanding, especially when cogging, show extra high resistance to deformation, low plasticity and very narrow texturing temperature interval, control the improper crackle that very easily occurs.Therefore must adopt suitable homogenizing treatment process, to improve the tissue of ingot casting.But because separating out mutually of alloy pig interdendritic complexity make homogenization process more complicated, must avoid that wherein low melting point is harmful to melt generation " burning " phenomenon in Homogenization Process.Must reduce in addition or eliminate element segregation, otherwise will cause follow-up hot-work and heat-treated sturcture inhomogeneous, seriously fall low-alloyed military service performance.
The Homogenization Treatment of existing GH742 alloy cast ingot is 1120～1150 ℃, 4～8h, and this system can not be eliminated dendritic segregation fully with mutually harmful, and rare-earth phase melts (Fig. 1) in this temperature range.Simultaneously, the thermal stable temperature of a MC type carbide is higher, after forging and pressing processing, generally all be broken and be band and be distributed in alloy inside (Fig. 2) along deformation direction, the alloy performance is harmful, and in bulk MC carbide shattering process, be easy to occur crackle (Fig. 3), reduced the hot-workability of alloy.Therefore, the as-cast structure that obtains homogeneous, segregation-free before ingot formation determines that namely the homogenizing treatment process of GH742 alloy cast ingot just seems especially important.
Summary of the invention
The homogenizing treatment process that the purpose of this invention is to provide a kind of high-alloying GH742 superalloy, two step homogenizing treatment steps of this process using low temperature pre-treatment plus high temperature diffusion, to improve the hot-workability of GH742 alloy cast ingot, reduce resistance to deformation, forging stock obtains evenly, recrystallized structure completely thereby make.
The invention provides a kind of homogenizing treatment process of high-alloying GH742 superalloy, concrete steps are as follows:
(1) the GH742 alloy cast ingot is warming up to 1050～1110 ℃ (being preferably 1080 ℃) with stove, average temperature rise rate be 200～400 ℃/h (be preferably 200 ℃/h), and be incubated 20～60h (being preferably 40h) with dissolving Ni
5Ce equates the low melting point phase;
(2) furnace temperature is increased to 1160～1200 ℃ (being preferably 1160 ℃), average temperature rise rate be 2～10 ℃/min (be preferably 2 ℃/min), and be incubated 20～60h (being preferably 60h) with the precipitated phase in the dissolving alloy and eliminate element segregation.Because the segregation of Nb is the most serious in the alloy, its Elements Diffusion coefficient is lower, and soaking time depends on segregation degree and the High temperature diffusion speed of Nb;
(3) will process rear ingot furnace and be as cold as below 500 ℃, take out air cooling to room temperature;
(4) after cooled ingot casting surface finish is smooth, carry out follow-up hammer cogging at forging hammer.
In conjunction with to the GH742 alloy cast ingot without homogenizing process, existing homogenization process (1140 ℃ * 6h) and the homogenization process that proposes of the present invention to carry out texturing temperature be 1120 ℃, strain rate is 0.01s
-1, deformation extent is 40% and 60% hot Compression Simulation distortion, so that advantage of the present invention to be described:
1) obtains to organize before the good cogging.Adopt technique of the present invention that " burning " do not occur, eliminated dendritic segregation and harmful precipitated phase of GH742 ingot casting, simultaneously, a MC carbide quantity is reduced, size decreases, the aggregation extent decrease, thus obtain the austenite structure (Fig. 4) of homogeneous, segregation-free.
2) improve the ingot casting hot-workability.Surface crack and internal tiny crack (Fig. 5) have appearred in the sample of processing, processing through 1140 ℃ * 6h homogenizing without homogenizing under 40% deformation extent, and crackle does not still appear in the sample deformation to 60% of processing through the present invention.
3) reduce resistance to deformation.The flow stress of sample in deformation process of processing through the present invention obviously reduces (Fig. 6), and the sample that its peak stress ratio is processed, processed through 1140 ℃ * 6h homogenizing without homogenizing has reduced respectively 27.5% and 21.0%.
4) recrystallized structure after the hot-work is even.Without homogenizing process, deformation bands appears in recrystallized structure behind the sample deformation that 1140 ℃ * 6h homogenizing is processed (Fig. 7 a), segregation line (Fig. 7 b), and behind the sample deformation that the present invention processes recrystallized structure evenly (Fig. 7 c).
Description of drawings
Fig. 1 is that rare-earth phase is at the pattern that fusing occurs more than 1120 ℃;
Fig. 2 is that ingot casting is once separated out the band tissue that forms after the distortion of MC type carbide;
Fig. 3 is for once separating out the tiny crack that the fragmentation of MC type carbide forms afterwards;
Fig. 4 is the tissue after art breading of the present invention;
Fig. 5 is out of shape the mutually broken tiny crack that forms of rear Laves without the ingot casting that homogenizing is processed;
Fig. 6 is without the homogenizing processing, through the processing of 1140 ℃ * 6h homogenizing and the true stress-true strain curve of sample in deformation process after art breading of the present invention;
Fig. 7 a-c is respectively without the homogenizing processing, through the processing of 1140 ℃ * 6h homogenizing and the recrystallized structure behind the sample deformation after the art breading of the present invention.
Embodiment
Following examples will be further described the present invention, but not thereby limiting the invention.
Embodiment 1
1) the GH742 alloy cast ingot is warming up to 1080 ℃ with stove, average temperature rise rate is 200 ℃/h, and insulation 40h is with dissolving Ni
5Ce equates the low melting point phase;
2) furnace temperature is increased to 1160 ℃, average temperature rise rate is 2 ℃/min, and insulation 60h is with the precipitated phase in the dissolving alloy and elimination element segregation.Because the segregation of Nb is the most serious in the alloy, its Elements Diffusion coefficient is lower, and soaking time depends on segregation degree and the High temperature diffusion speed of Nb;
3) will process rear ingot furnace and be as cold as below 500 ℃, take out air cooling to room temperature;
4) after cooled ingot casting surface finish is smooth, carry out follow-up hammer cogging at forging hammer.
Embodiment 2
1) the GH742 alloy cast ingot is warming up to 1110 ℃ with stove, average temperature rise rate is 400 ℃/h, and insulation 20h is with dissolving Ni
5Ce equates the low melting point phase;
2) furnace temperature is increased to 1200 ℃, average temperature rise rate is 10 ℃/min, and insulation 20h is with the precipitated phase in the dissolving alloy and elimination element segregation.Because the segregation of Nb is the most serious in the alloy, its Elements Diffusion coefficient is lower, and soaking time depends on segregation degree and the High temperature diffusion speed of Nb;
3) will process rear ingot furnace and be as cold as below 500 ℃, take out air cooling to room temperature;
4) after cooled ingot casting surface finish is smooth, carry out follow-up hammer cogging at forging hammer.
Embodiment 3
1) the GH742 alloy cast ingot is warming up to 1050 ℃ with stove, average temperature rise rate is 300 ℃/h, and insulation 60h is with dissolving Ni
5Ce equates the low melting point phase;
2) furnace temperature is increased to 1180 ℃, average temperature rise rate is 5 ℃/min, and insulation 40h is with the precipitated phase in the dissolving alloy and elimination element segregation.Because the segregation of Nb is the most serious in the alloy, its Elements Diffusion coefficient is lower, and soaking time depends on segregation degree and the High temperature diffusion speed of Nb;
3) will process rear ingot furnace and be as cold as below 500 ℃, take out air cooling to room temperature;
4) after cooled ingot casting surface finish is smooth, carry out follow-up hammer cogging at forging hammer.
Claims (7)
1. the homogenizing treatment process of a high-alloying GH742 superalloy, it is characterized in that: concrete steps are as follows:
(1) the GH742 alloy cast ingot is warming up to 1050～1110 ℃ with stove, average temperature rise rate is 200～400 ℃/h, and is incubated 20～60h;
(2) furnace temperature is increased to 1160～1200 ℃, average temperature rise rate is 2～10 ℃/min, and is incubated 20～60h;
(3) will process rear ingot furnace and be as cold as below 500 ℃, take out air cooling to room temperature;
(4) after cooled ingot casting surface finish is smooth, carry out follow-up hammer cogging at forging hammer.
2. according to the homogenizing treatment process of the described high-alloying GH742 of claim 1 superalloy, it is characterized in that: in the described step (1) the GH742 alloy cast ingot is warming up to 1080 ℃ with stove.
3. according to the homogenizing treatment process of the described high-alloying GH742 of claim 1 superalloy, it is characterized in that: the average temperature rise rate in the described step (1) is 200 ℃/h.
4. according to the homogenizing treatment process of the described high-alloying GH742 of claim 1 superalloy, it is characterized in that: the soaking time in the described step (1) is 40h.
5. according to the homogenizing treatment process of the described high-alloying GH742 of claim 1 superalloy, it is characterized in that: in the described step (2) furnace temperature is increased to 1160 ℃.
6. according to the homogenizing treatment process of the described high-alloying GH742 of claim 1 superalloy, it is characterized in that: the average temperature rise rate in the described step (2) is 2 ℃/min.
7. according to the homogenizing treatment process of the described high-alloying GH742 of claim 1 superalloy, it is characterized in that: the soaking time in the described step (2) is 60h.
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Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104762574A (en) * | 2015-03-29 | 2015-07-08 | 北京工业大学 | Homogenizing treatment method of Al-Zn-Mg alloy semi-continuous casting round ingot for high-speed rails |
| CN105331913A (en) * | 2015-12-09 | 2016-02-17 | 兰州理工大学 | Method for thermally extruding and deforming high-temperature alloy Inconel 625 pipe through short process |
| CN107523772A (en) * | 2016-06-22 | 2017-12-29 | 中国科学院金属研究所 | A kind of homogenization process of U720Li high temperature alloys |
| CN110423960A (en) * | 2019-08-06 | 2019-11-08 | 北京科技大学 | A kind of Ni alloy ingot homogenization process of the high cobalt of high tungsten |
| CN111719039A (en) * | 2019-03-22 | 2020-09-29 | 上海电气电站设备有限公司 | FeCoNiAlNb high-temperature alloy homogenization treatment method |
| CN112176266A (en) * | 2020-09-04 | 2021-01-05 | 北京科技大学 | Control method of GH4105 nickel-based alloy carbide strip structure |
| CN113943909A (en) * | 2021-10-21 | 2022-01-18 | 成都先进金属材料产业技术研究院股份有限公司 | Method for improving thermoplasticity of GH141 high-temperature alloy difficult to deform |
| CN113981274A (en) * | 2021-10-26 | 2022-01-28 | 中国华能集团有限公司 | Two-stage homogenization heat treatment method for high-strength nickel-based high-temperature alloy cast ingot |
| CN114045436A (en) * | 2021-11-12 | 2022-02-15 | 成都先进金属材料产业技术研究院股份有限公司 | GH2909 alloy ingot and preparation method thereof |
| CN114086032A (en) * | 2021-11-12 | 2022-02-25 | 成都先进金属材料产业技术研究院股份有限公司 | GH4065A nickel-based high-temperature alloy and homogenization treatment process |
| CN114318191A (en) * | 2021-11-26 | 2022-04-12 | 西安聚能高温合金材料科技有限公司 | Homogenization treatment method of nickel-based superalloy GH4169G alloy |
-
2012
- 2012-04-05 CN CN2012100980392A patent/CN103361585A/en active Pending
Non-Patent Citations (1)
| Title |
|---|
| 潘晓林等: "《均匀化过程中铸态GH742合金的组织转变》", 《材料研究学报》 * |
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104762574A (en) * | 2015-03-29 | 2015-07-08 | 北京工业大学 | Homogenizing treatment method of Al-Zn-Mg alloy semi-continuous casting round ingot for high-speed rails |
| CN105331913A (en) * | 2015-12-09 | 2016-02-17 | 兰州理工大学 | Method for thermally extruding and deforming high-temperature alloy Inconel 625 pipe through short process |
| CN107523772A (en) * | 2016-06-22 | 2017-12-29 | 中国科学院金属研究所 | A kind of homogenization process of U720Li high temperature alloys |
| CN107523772B (en) * | 2016-06-22 | 2019-06-11 | 中国科学院金属研究所 | A kind of homogenization process of U720Li high temperature alloy |
| CN111719039A (en) * | 2019-03-22 | 2020-09-29 | 上海电气电站设备有限公司 | FeCoNiAlNb high-temperature alloy homogenization treatment method |
| CN110423960A (en) * | 2019-08-06 | 2019-11-08 | 北京科技大学 | A kind of Ni alloy ingot homogenization process of the high cobalt of high tungsten |
| CN112176266A (en) * | 2020-09-04 | 2021-01-05 | 北京科技大学 | Control method of GH4105 nickel-based alloy carbide strip structure |
| CN112176266B (en) * | 2020-09-04 | 2022-01-18 | 北京科技大学 | Control method of GH4105 nickel-based alloy carbide strip structure |
| CN113943909A (en) * | 2021-10-21 | 2022-01-18 | 成都先进金属材料产业技术研究院股份有限公司 | Method for improving thermoplasticity of GH141 high-temperature alloy difficult to deform |
| CN113981274A (en) * | 2021-10-26 | 2022-01-28 | 中国华能集团有限公司 | Two-stage homogenization heat treatment method for high-strength nickel-based high-temperature alloy cast ingot |
| CN114045436A (en) * | 2021-11-12 | 2022-02-15 | 成都先进金属材料产业技术研究院股份有限公司 | GH2909 alloy ingot and preparation method thereof |
| CN114086032A (en) * | 2021-11-12 | 2022-02-25 | 成都先进金属材料产业技术研究院股份有限公司 | GH4065A nickel-based high-temperature alloy and homogenization treatment process |
| CN114318191A (en) * | 2021-11-26 | 2022-04-12 | 西安聚能高温合金材料科技有限公司 | Homogenization treatment method of nickel-based superalloy GH4169G alloy |
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Application publication date: 20131023 |