CN114058989A - Method for improving high-temperature strength of precipitation-strengthened high-temperature alloy - Google Patents
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Abstract
The invention provides a method for improving the high-temperature strength of a precipitation-strengthened high-temperature alloy, and relates to the technical field of regulation and control of structural properties of high-temperature alloys. Carrying out first solution treatment on the precipitation strengthening type high-temperature alloy to obtain a single gamma-phase solid solution alloy; carrying out ultrasonic rolling or shot blasting on the single gamma-phase solid solution alloy to form a deformation layer on the surface of the single gamma-phase solid solution alloy to obtain a deformation alloy; the hardness of the deformation layer is gradually reduced from the surface to the core; and (3) carrying out aging treatment on the wrought alloy, precipitating a second phase with gradient distribution from the surface to the core of the deformation layer, and gradually reducing the quantity of the second phase from the surface to the core. The invention can improve the high-temperature strength of the precipitation strengthening type high-temperature alloy without changing the alloy components.
Description
Technical Field
The invention relates to the technical field of regulation and control of structural properties of a high-temperature alloy, in particular to a method for improving the high-temperature strength of a precipitation-strengthened high-temperature alloy.
Background
The precipitation strengthening type high-temperature alloy is a main alloy material for aerospace, and is widely applied to shaft parts, disc parts, fasteners and the like of an aircraft engine. Along with the increase in the power of an aircraft engine, in addition to the requirement for good heat dissipation, the high temperature performance of the materials from which the components are made is also required. Typically 650 ℃ is used as the test temperature standard, and some also require high temperature mechanical property testing at 704 ℃ (such as Inconel 718 PLUS). The higher the high temperature mechanical properties, the higher the temperature that can be withstood. Therefore, the high-temperature strength of the material is always pursued by the industries of aeroengines and thermal engineering.
At present, the high-temperature alloy material which is commonly used is usually added with noble metal elements (such as Co and the like) to improve the high-temperature strength, and the cost is higher.
Disclosure of Invention
The invention aims to provide a method for improving the high-temperature strength of a precipitation strengthening type high-temperature alloy, which can improve the high-temperature strength of the precipitation strengthening type high-temperature alloy without changing alloy components.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides a method for improving the high-temperature strength of a precipitation-strengthened high-temperature alloy, which comprises the following steps:
carrying out first solution treatment on the precipitation strengthening type high-temperature alloy to obtain a single gamma-phase solid solution alloy;
carrying out ultrasonic rolling or shot blasting on the single gamma-phase solid solution alloy to form a deformation layer on the surface of the single gamma-phase solid solution alloy to obtain a deformation alloy; the hardness of the deformation layer is gradually reduced from the surface to the core;
and (3) carrying out aging treatment on the wrought alloy, precipitating a second phase with gradient distribution from the surface to the core of the deformation layer, and gradually reducing the quantity of the second phase from the surface to the core.
Preferably, the temperature of the first solution treatment is 980 to 1060 ℃.
Preferably, the heat preservation time of the first solution treatment is 30-120 min.
Preferably, before the aging treatment, the method further comprises the step of carrying out second solution treatment on the wrought alloy; and a second phase is precipitated from the core of the wrought alloy in the second solution treatment process.
Preferably, the thickness of the deformation layer is 100-400 μm.
Preferably, the precipitation-strengthened superalloy comprises a nickel-based superalloy.
Preferably, the nickel-base superalloy comprises a GH4169 alloy or an Inconel 718 alloy.
Preferably, when the precipitation strengthening superalloy is a GH4169 alloy, the aging treatment comprises: performing first aging treatment at 720 ℃ for 8h, and then cooling to 620 ℃ for second aging treatment for 8 h;
when the precipitation strengthened superalloy is an Inconel 718 alloy, the aging process comprises: and (3) carrying out aging treatment at 788 ℃ for 8 h.
Preferably, when the precipitation strengthening type high-temperature alloy is GH4169 alloy, the temperature of the second solution treatment is 960-980 ℃;
when the precipitation strengthening type high-temperature alloy is Inconel 718 alloy, the temperature of the second solution treatment is 954-982 ℃.
The invention provides a method for improving the high-temperature strength of a precipitation-strengthened high-temperature alloy, which comprises the following steps: carrying out first solution treatment on the precipitation strengthening type high-temperature alloy to obtain a single gamma-phase solid solution alloy; carrying out ultrasonic rolling or shot blasting on the single gamma-phase solid solution alloy to form a deformation layer on the surface of the single gamma-phase solid solution alloy to obtain a deformation alloy; the hardness of the deformation layer is gradually reduced from the surface to the core; and (3) carrying out aging treatment on the wrought alloy, precipitating a second phase with gradient distribution from the surface to the core of the deformation layer, and gradually reducing the quantity of the second phase from the surface to the core.
The invention firstly carries out first solution treatment on a precipitation strengthening type high-temperature alloy to obtain a single gamma-phase solid solution alloy, then carries out ultrasonic rolling or shot blasting on the single gamma-phase solid solution alloy to form a deformation layer on the surface of the single gamma-phase solid solution alloy, wherein the deformation layer has large surface distortion degree and gradually reduces deformation towards a centripetal part (specifically, the deformation layer has high surface hardness and gradually reduces hardness towards the centripetal part), the deformation layer has the characteristic of strain-induced precipitation relative to a second phase (also called a stable intermediate phase, the second phase refers to a delta phase in GH4169 alloy, and the second phase refers to an eta phase in Inconel 718PLUS), therefore, in the subsequent aging treatment process, according to the gradient of deformation in the deformation layer, the second phase with gradient distribution is precipitated, specifically, the number of the second phase on the surface of the alloy is large, the number of the centripetal part is gradually reduced, on the one hand, a constraint layer can be formed in an enrichment region of the second phase on the surface, the deformation of other local areas under high-temperature load is restrained, and on the other hand, because the second phase is precipitated in a gradient manner, a stress concentration interface can not appear, so that the high-temperature strength can be effectively improved.
Drawings
FIG. 1 is a schematic view of a microstructure of a phase gradient precipitation sample during tensile deformation;
FIG. 2 is a microstructure of an alloy of example 1GH4169 after solution treatment;
FIG. 3 is a microstructure comparison of aged samples of examples 1 and 2;
FIG. 4 is a plot of delta phase volume fraction and dimensional change of USRP samples of the alloys treated in examples 1-2 from different depths in the surface layer;
FIG. 5 is a tensile curve at 650 ℃ of the samples of examples 1 to 2 and comparative example 1;
FIG. 6 is a histogramming diagram of the eta-phase gradient distribution of example 3 after a second solution treatment;
FIG. 7 is a grain size gradient distribution diagram of the eta-phase from the surface to the core after the second solution treatment in example 3;
FIG. 8 is a graph showing tensile curves of the samples of example 3 and comparative example 2 at 704 ℃.
Detailed Description
The invention provides a method for improving the high-temperature strength of a precipitation-strengthened high-temperature alloy, which comprises the following steps:
carrying out first solution treatment on the precipitation strengthening type high-temperature alloy to obtain a single gamma-phase solid solution alloy;
carrying out ultrasonic rolling or shot blasting on the single gamma-phase solid solution alloy to form a deformation layer on the surface of the single gamma-phase solid solution alloy to obtain a deformation alloy; the hardness of the deformation layer is gradually reduced from the surface to the core;
and (3) carrying out aging treatment on the wrought alloy, precipitating a second phase with gradient distribution from the surface to the core of the deformation layer, and gradually reducing the quantity of the second phase from the surface to the core.
The method carries out first solution treatment on the precipitation strengthening type high-temperature alloy to obtain single gamma-phase solid solution alloy.
In the invention, the precipitation strengthening type high-temperature alloy refers to a high-temperature alloy which forms a dispersed fine strengthening phase in a matrix through solid solution and aging so as to meet the dispersion strengthening requirement. It is noted that the precipitation-strengthened superalloy relies on a strengthening phase for strengthening, whereas the second phase described herein is not a strengthening phase, but a stabilizing phase for the nail-rolling grain boundaries. The present invention does not require any particular type of precipitation-strengthened superalloy, and precipitation-strengthened superalloys known in the art are also suitable. In an embodiment of the present invention, the precipitation strengthened superalloy is a nickel-based superalloy, specifically, a GH4169 alloy or an Inconel 718 alloy.
In the invention, the temperature of the first solution treatment is preferably 980-1060 ℃, more preferably 1000-1050 ℃, and further preferably 1020-1040 ℃; the heat preservation time of the first solution treatment is preferably 30-120 min. In the invention, the proper heat preservation time is preferably selected within the range according to the size of the precipitation strengthening type superalloy so as to ensure full solid solution. In the invention, after the first solution treatment, all strengthening phases and delta phases are dissolved back to obtain a complete solid solution with lower strength, and a single gamma-phase solid solution alloy is obtained.
After the single gamma-phase solid solution alloy is obtained, carrying out ultrasonic rolling or shot blasting on the single gamma-phase solid solution alloy to form a deformation layer on the surface of the single gamma-phase solid solution alloy to obtain a deformation alloy; the hardness of the deformation layer is gradually reduced from the surface to the core.
The invention has no special requirements on the conditions of ultrasonic rolling and shot blasting, and the deformation layer can be obtained by adopting the conditions of ultrasonic rolling and shot blasting which are well known in the field. In an embodiment of the present invention, the ultrasonic rolling conditions include: the marble pressure is 0.12Mpa, the impact frequency is 27kHz, the rotating speed is 180r/min, the invention is matched with compressed gas to lead the marble to vibrate rapidly and repeatedly, and the marble impacts the surface of the solid solution alloy at higher frequency. In the present invention, the shot blasting preferably uses compressed gas or liquid as a medium, the medium contains 50 to 100 μm-diameter shots, and the shots are ejected at a rate of 100m/s and hit the surface of the solid solution alloy, so that the surface layer of the solid solution alloy deforms when the shots strike. The invention preferably carries out ultrasonic rolling or shot blasting for multiple times so as to ensure that a deformation layer is obtained; the number of times of ultrasonic rolling or shot blasting is preferably 3-6 times.
In the present invention, the thickness of the deformation layer is preferably 100 to 400 μm, more preferably 150 to 350 μm, and further preferably 200 to 300 μm. In the invention, the metal distortion degree of the deformation layer from the surface to the core part is gradually reduced, so the hardness is also distributed in a gradient way along with the metal distortion degree, and the hardness is gradually reduced from the surface to the core part. In the embodiment of the invention, when the precipitation strengthening type high temperature alloy is GH4169 alloy, the surface hardness of the deformation layer is 430-450 HV, the deformation layer gradually weakens towards the heart, and the hardness is reduced to 230HV at the deep layer of 250-300 μm.
After obtaining the wrought alloy, the invention carries out aging treatment on the wrought alloy (scheme one), or carries out second solution treatment and aging treatment on the wrought alloy in sequence (scheme two).
The first embodiment will be explained below.
The invention carries out aging treatment on the wrought alloy.
In the present invention, the aging treatment conditions are preferably the normal aging conditions for the precipitation-strengthened superalloy. Conventional aging conditions for the precipitation strengthened superalloy are common knowledge in the art. For example, when the precipitation-strengthened superalloy is a GH4169 alloy, its conventional aging includes: the first aging treatment is carried out for 8h at the temperature of 720 ℃, and then the second aging treatment is carried out for 8h after the temperature is reduced to 620 ℃. When the precipitation-strengthened superalloy is an Inconel 718 alloy, its conventional aging is: and (3) carrying out aging treatment at 788 ℃ for 8 h.
When aging treatment is carried out, a second phase is not precipitated from a normal sample, but the precipitation of the second phase is promoted by a deformation layer on the surface of the alloy under the condition of strain induction, so that the second phase is precipitated from the deformation layer in a gradient manner under the aging treatment condition, specifically, the number of the second phase on the surface is large, the number of the second phase in the deformation layer in the centripetal part direction is gradually reduced, and a strengthening phase is normally precipitated from the core part (when the precipitation strengthening type high-temperature alloy is GH4169 alloy, the strengthening phase refers to a gamma ' phase and a gamma ' phase, and when the precipitation strengthening type high-temperature alloy is Inconel 718 alloy, the strengthening phase refers to a gamma ' phase); meanwhile, the size of the second phase crystal grains in the deformation layer gradually increases along with the increase of the depth, the surface layer is fine crystal grains obtained by processing, and the size of the crystal grains increases to the core part, so the fine crystal grains of the surface layer in the method are of a gradient structure. As shown in fig. 1, a large number of second phases (white short bars in the figure) precipitated on the surface layer block the movement of dislocations to pin the grain boundaries, resulting in that the deformation of the surface layer is suppressed during the drawing process, while the number of second phases in the core is reduced, the block on the slip system is reduced, and more slip systems (such as black line segments in the core grains) are started. Thereby forming the structural characteristic that the core strain is restrained by the surface, but the dislocation density is gradually changed. The dark surface to lighter matrix indicates that the geometrically necessary dislocation density varies from high to low under this structural condition. In general, the second phase precipitated in a gradient way forms a constraint layer to constrain the deformation of other local areas under high-temperature load, and a stress concentration interface cannot appear, so that the high-temperature strength can be effectively improved. The second solid solution and aging treatment are carried out compared with the second scheme, the second phase precipitated in the first scheme is finer, and the second phase has better strength and plasticity compared with the second scheme; compared with the conventional solid solution and aging treatment mode, the high-temperature strength and plasticity of the scheme I are improved more obviously.
In the present invention, when the precipitation strengthening superalloy is a GH4169 alloy, the second phase is a delta phase; when the precipitation-strengthened superalloy is an Inconel 718 alloy, the second phase is an eta phase.
Scheme two is explained below.
The invention carries out the second solution treatment and the aging treatment on the wrought alloy in sequence.
In the present invention, the conditions of the second solution treatment are preferably normal solution conditions of the precipitation-strengthened superalloy. In the present invention, the conventional solid solution conditions of the precipitation-strengthened superalloy are common knowledge in the art. Specifically, when the precipitation strengthening type high-temperature alloy is GH4169 alloy, the temperature of the second solution treatment is 960-980 ℃, and the heat preservation time is 60-90 min; when the precipitation strengthening type high-temperature alloy is Inconel 718 alloy, the temperature of the second solution treatment is 954-982 ℃, and the heat preservation time is 60-90 min.
In the present invention, the temperature of the second solution treatment is the normal solution temperature, which can promote the core of the wrought alloy to precipitate the second phase (mainly referring to the undeformed core), but the temperature is higher than that of the surface deformation layer, so the size of the second phase precipitated by gradient of the deformation layer of the second solution treatment is larger, the performance improvement is not good as that of the first solution treatment, the high-temperature strength is improved compared with the normal solution + aging, but the plasticity is worse than that of the first solution treatment, and is equivalent to or slightly worse than that of the normal solution + aging.
In the present invention, the aging treatment conditions are the same as those in the first embodiment, and are not described herein again.
In the aging treatment process, the whole matrix of the wrought alloy is precipitated with strengthening phases.
The method for improving the high temperature strength of the precipitation strengthening type superalloy provided by the present invention will be described in detail with reference to the following examples, but the method is not to be construed as limiting the scope of the present invention.
Example 1
Carrying out solution treatment on GH4169 alloy, wherein the solution heating temperature is 1020 ℃, the heat preservation time is 60min, then rapidly cooling to obtain a uniform single-phase solution structure, and as shown in figure 2, the surface hardness index is a range value because the redissolution of a strengthening phase is reduced to 225-250 HV (hardness test is carried out on a plurality of areas of the surface);
shot blasting is carried out on the obtained solid solution alloy, the diameter of the shot is 60 mu m, the shot is ejected at the speed of 100m/s, continuous feeding is carried out, 4 times of repeated shot blasting is carried out, a deformation layer is formed on the surface, the maximum hardness of the surface is 430-450 HV, the deformation layer is gradually weakened towards the centripetal part, the hardness is reduced to 230HV in the deep layer, and the deformation alloy is obtained;
the wrought alloy was then directly aged at 720 ℃ for 8h +620 ℃ for 8h, which was reported as 1# aging.
Example 2
The difference from example 1 is that the wrought alloy is subjected to solution treatment at 960 ℃ for 60 minutes, and then subjected to aging treatment at 720 ℃ for 8 hours +620 ℃ for 8 hours, which is recorded as 2# aging mode.
Comparative example 1
Adopts a conventional solution aging treatment mode, namely, the GH4169 alloy is directly subjected to solution treatment at 960 ℃ for 60 minutes and then subjected to aging treatment at 720 ℃ for 8h +620 ℃ for 8 h.
Structure and performance testing
1. The microstructure of the aged samples of examples 1 and 2 was observed, and the results are shown in FIG. 3. In fig. 3, (a) the 1# aging system, (b) the 2# aging system, (c) the 1# aging system, and (d) the 2# aging system.
As shown in FIG. 3 (a) and (c), the aging treatment at 720 ℃ for 8h +620 ℃ for 8h is directly performed in the 1# aging mode, and the distortion energy of the deformation layer promotes the gradient precipitation of the delta phase from the surface to the core portion by 200 to 300 μm, and the sufficient strengthening phase gamma 'phase and gamma' phase are precipitated in the core portion through the aging treatment.
As shown in fig. 3 (b) and (d), the aging method 2# first performed a solution treatment at 960 ℃ and then performed an aging treatment at 720 ℃ for 8h +620 ℃ for 8h, which also formed a gradient structure of the δ phase in the surface layer, but unlike the aging method 1# the aging method 2# had a coarser δ phase and a smaller amount of δ phase in the core, which satisfied the structure conditions required for the δ phase in the core.
2. FIG. 4 is a plot of delta phase volume fraction and dimensional change from different depths in the surface layer for USRP test specimens of alloys treated in examples 1-2, wherein (a)1# aging mode and (b)2# aging mode. As can be seen from fig. 4, as the distance from the surface of the superalloy increases, the crystal grain size of the δ -phase gradually increases and the volume fraction gradually decreases.
3. The samples of examples 1-2 and comparative example 1 were subjected to mechanical property test at 650 ℃ and the high temperature tensile curve is shown in FIG. 5. As can be seen from fig. 5, the tensile strength and plasticity of the sample treated by the solution aging treatment are better in # 1 and higher in # 2. Specific data corresponding to fig. 5 are shown in table 1.
TABLE 1 examples 1-2 and comparative example 1 sample tensile properties at 650 deg.C
| Test specimen | Conventional solid solution aging |
1# aging mode | 2# aging mode |
| Tensile strength (MPa) | 989 | 1105 | 1098 |
| Yield strength (MPa) | 853 | 1022 | 1004 |
| Elongation (%) | 22.32 | 34.82 | 19.22 |
Example 3
After the Inconel 718PLUS alloy is subjected to heat preservation at 1030 ℃ for 1h to complete first solution treatment, a marble with the pressure of 0.12Mpa is adopted for ultrasonic rolling, the impact frequency is 27kHz, the rotating speed is 180r/min, continuous feeding is carried out, rolling is carried out for 4 times, a deformation layer is formed on the surface, then secondary solution at 960 ℃ is carried out, the precipitation of a second phase eta phase in the deformation layer is promoted, and the texture characteristic of the gradient distribution of the surface eta phase is formed, and the structure is shown in figure 6; and the grain size gradient distribution from the surface to the core is shown in FIG. 7; then aging is carried out for 788 ℃ for 8h +704 ℃ for 8h to finish the treatment.
Comparative example 2
The difference from example 3 is that the Inconel 718PLUS alloy was subjected to conventional solution ageing treatment, i.e. heat preservation directly at 960 ℃ followed by ageing 788 ℃ 8h +704 ℃ 8h to finish the treatment.
The high-temperature tensile property is carried out at 704 ℃ according to the requirement of a 718PLUS high-temperature tensile test, the high-temperature tensile strength is 968.18MPa after conventional heat treatment, the elongation index of the Inconel 718PLUS alloy subjected to eta-phase gradient precipitation is slightly reduced (from 15.5 percent to 13.5 percent), but the high-temperature tensile strength is improved to 1019.95MPa, the high-temperature performance is obviously improved, and a specific high-temperature tensile curve is shown in figure 8.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.
Claims (9)
1. A method for improving the high-temperature strength of a precipitation strengthening type high-temperature alloy is characterized by comprising the following steps:
carrying out first solution treatment on the precipitation strengthening type high-temperature alloy to obtain a single gamma-phase solid solution alloy;
carrying out ultrasonic rolling or shot blasting on the single gamma-phase solid solution alloy to form a deformation layer on the surface of the single gamma-phase solid solution alloy to obtain a deformation alloy; the hardness of the deformation layer is gradually reduced from the surface to the core;
and (3) carrying out aging treatment on the wrought alloy, precipitating a second phase with gradient distribution from the surface to the core of the deformation layer, and gradually reducing the quantity of the second phase from the surface to the core.
2. The method according to claim 1, wherein the temperature of the first solution treatment is 980 to 1060 ℃.
3. The method according to claim 1 or 2, wherein the holding time of the first solution treatment is 30 to 120 min.
4. The method of claim 1, further comprising, prior to the aging, subjecting the wrought alloy to a second solution treatment; and a second phase is precipitated from the core of the wrought alloy in the second solution treatment process.
5. The method according to claim 1, wherein the thickness of the transformation layer is 100 to 400 μm.
6. The method of claim 1, wherein the precipitation-strengthened superalloy comprises a nickel-based superalloy.
7. The method of claim 6, wherein the nickel-base superalloy comprises a GH4169 alloy or an Inconel 718 alloy.
8. The method of claim 7, wherein when the precipitation-strengthened superalloy is a GH4169 alloy, the aging comprises: performing first aging treatment at 720 ℃ for 8h, and then cooling to 620 ℃ for second aging treatment for 8 h;
when the precipitation strengthened superalloy is an Inconel 718 alloy, the aging process comprises: and (3) carrying out aging treatment at 788 ℃ for 8 h.
9. The method according to claim 4 or 7, wherein when the precipitation-strengthened superalloy is a GH4169 alloy, the temperature of the second solution treatment is 960-980 ℃;
when the precipitation strengthening type high-temperature alloy is Inconel 718 alloy, the temperature of the second solution treatment is 954-982 ℃.
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