CN115896585B - A density lower than 8.0g/cm 3 Is a deformation high-strength high Wen Gaoshang alloy and a preparation method thereof - Google Patents
A density lower than 8.0g/cm 3 Is a deformation high-strength high Wen Gaoshang alloy and a preparation method thereof Download PDFInfo
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Abstract
The invention provides a material with a density of less than 8.0g/cm 3 The deformation high-strength high Wen Gaoshang alloy belongs to the field of low-density deformation high-Wen Gaoshang alloy, and comprises Ni, co, fe, cr, mo, al, ti, nb, C, B, zr elements, wherein the mass percent (wt.%) of the alloy components are as follows, co:9.3 to 15.5, fe:5.8 to 11.8, cr:15.5 to 17.8, mo:2.5 to 3.0, al:2.5 to 3.5, ti:2.0 to 3.0, nb: 0.98-3.0, C:0.02 to 0.05, B: 0.005-0.015, zr:0.02 to 0.03, ni: the balance, and the atomic percentage ratio of (Ti+Nb)/Al is 0.5-1. The invention realizes that the alloy density is lower than 8.0g/cm through alloy design 3 At the same time L1 2 The gamma ' phase particles are co-precipitated on the FCC-gamma matrix, the total volume percentage of the gamma ' phase is 30-45%, and the alloy shows excellent gamma/gamma ' co-structural stability after long-term aging at 750 ℃ without other harmful phase precipitation, so that the alloy has good mechanical property and excellent processing deformability, the room temperature plasticity is more than 18%, and the yield strength at 750 ℃ is more than 800MPa, and is a novel low-density deformation high-strength high-Wen Gaoshang alloy.
Description
Technical Field
The invention belongs to the field of low-density deformation high Wen Gaoshang alloy, in particular to a high-density alloy with the density lower than 8.0g/cm 3 The deformed high-strength high Wen Gaoshang alloy and the preparation method thereof can keep stable FCC-gamma/gamma' coherent structure after long-term aging at 750 ℃, and the high-temperature strength at the temperature exceeds 800MPa.
Background
The high-temperature alloy is based on Fe, co and Ni, and usually works under the high temperature of 600-1200 ℃ and complex stress, and the severe environment has strict requirements on various physical, chemical and mechanical properties of the alloy. The superalloy must have high heat resistance, good plasticity, high temperature oxidation resistance, corrosion resistance, and long-term tissue thermal stability. With the rapid development of the aerospace industry, the thrust-weight ratio of the aircraft is increased, the working temperature of engine parts is continuously increased, and the development and application of the deformed superalloy for the turbine disc are promoted. In order to meet the working condition requirements of the aero-engine, the temperature bearing capacity of the high-temperature alloy for the turbine disc is increased to be more than 700 ℃. In order to improve the service performance of the alloy and meet the requirement of high-temperature strength, a large amount of solid solution strengthening elements (W, mo), gamma' phase forming elements (Al, ti and Nb) and fault energy elements (Co and Ta) are added into the deformed high-temperature alloy for the high-performance turbine disk. However, the high alloying degree not only increases the preparation cost of the alloy, but also increases the difficulty in regulating and controlling the processing deformation and the structural performance of the alloy, and meanwhile, as elements with large specific gravity such as W, ta and the like are added and the content of precipitated phases is increased to improve the strength of the alloy, the Ti/Al ratio is increased, the density of the alloy is greatly increased, and the thrust-weight ratio and the weight reduction of an aircraft are one of key technical means.
The deformation high-temperature alloy material for the existing turbine disk in China is difficult to break through 750 ℃, and meanwhile, the alloy density is higher due to high alloying elements, and the alloy density is generally 8.2g/cm 3 The above. For example, a wrought superalloy typified by In718 has excellent workability and deformability, and is excellent In terms of high Nb content (4.75 to 5.50 wt.%) and is characterized by slow Nb element diffusion, slow nucleation rate of a precipitated phase, low precipitation temperature and a large hot working window, but the alloy element segregation is easily caused by a higher Nb content, and the use temperature of the In718 alloy is limited to 650 ℃, and once the temperature is raised, phase transformation occurs, so that the phase transformation mainly strengthens γ "-Ni of a tetragonal structure of the phase 3 Nb will be converted into quadrature structure delta-Ni 3 Nb greatly reduces alloy performance due to the fact that the co-operation relationship with the matrix FCC-gamma phase is lost; then the In718Plus alloy increases the Al content by increasing Co, W and other temperature-bearing elements, so that ordered L1 is precipitated on the FCC-gamma matrix 2 The gamma-nanometer particles form FCC-gamma/gamma-coherent structures with stable high-temperature structures, so that the temperature resistance of the alloy is improved to 700 ℃, but the processing deformation capacity of the alloy is weaker than In718, in particular to the elongation after fracture of a cold-rolled sheet<10%; japanese national standardThe temperature bearing capacity of the Ni-Co-based TMW superalloy developed by the material science research can reach 725 ℃, wherein the Co content is 20-31 wt%, the Ti content is 5.1-7.4 wt%, and the W content is 1.0-2.0 wt%, so that the alloy temperature bearing capacity is improved to a certain extent, but when the Ti content is higher than 6.0 wt%, eta-Ni can be precipitated 3 Ti deleterious phase, affecting alloy properties, and the alloy density>8.0g/cm 3 In addition, the content of gamma 'particles reaches 45-50%, and at the moment, the gamma' phase precipitation temperature is high, the hot working window is narrow, and the method belongs to the category of refractory high-temperature alloys.
In the invention of CN102443721A, a nickel-cobalt-based superalloy with good tissue stability and easy processing is proposed by the national academy of sciences metal research. The alloy is characterized in that Ru (0.1-10 wt%) element is added on the basis of TMW, so that precipitation of eta harmful phase can be inhibited, but a large amount of Co element (22-35 wt%) is still added in the alloy, and the alloy also contains heavy elements such as W (0.1-5.0 wt%) and Ta (0.1-5.0 wt%) and the like, so that the alloy cost is greatly increased, and the alloy density is increased; in addition, the high Ti/Al ratio (3-10 wt.% Ti, 0.2-5 wt.% Al, atomic percent ratio > 1.5) in the alloy can improve the precipitation amount of gamma 'particles to a certain extent, but also improve the precipitation temperature of gamma' phase, which reduces the hot working window and leads to the improvement of the working difficulty; more importantly, the invention only reports the room temperature compression performance of the alloy, the compression yield strength is not more than 1000MPa, and the room temperature and high temperature tensile performance and the high temperature tissue stability of the alloy are not reported.
The existing commercial cast-forging deformation alloy has the advantages of simple preparation process, low cost, large deformation difficulty, poor structure uniformity, insufficient temperature bearing capability and large density>8.0g/cm 3 ) Even part of the Co-based superalloy GH5188, GH605 density has exceeded 9.0g/cm 3 The comprehensive performance is difficult to improve.
Thus, two core problems that limit the development of current wrought superalloys: on one hand, the alloy ensures the high temperature bearing capacity and the high temperature structure stability of the alloy and simultaneously ensures the low density; on the other hand, while improving the high temperature performance of the alloy, excellent deformability is ensured. In view of this, the present invention provides a low densityAt 8.0g/cm 3 The deformation high-strength high Wen Gaoshang alloy and the preparation method thereof can keep the stable gamma/gamma' coherent structure after long-term aging at 750 ℃, have no harmful phase precipitation and have room-temperature tensile yield strength>1050MPa, plasticity>18%, high temperature strength at 750 DEG C>800MPa。
Disclosure of Invention
The invention provides a material with a density of less than 8.0g/cm 3 The deformed high-strength high Wen Gaoshang alloy has higher alloy density than the prior cast-forging deformed high-temperature alloy and the preparation method thereof<8.0g/cm 3 High temperature yield strength at 750 DEG C>And after 800MPa and long-term aging, the gamma/gamma' coherent structure is stable, and no harmful phase is separated out. The invention aims to develop a novel deformation high-strength high-Wen Gaoshang alloy with lower density and higher temperature bearing capacity for aerospace through accurate alloy design.
In order to achieve the above purpose, the invention adopts the following technical scheme:
a density lower than 8.0g/cm 3 A deformed high strength high Wen Gaoshang alloy having a density of less than 8.0g/cm 3 The deformation high-strength high Wen Gaoshang alloy of (1) comprises Ni, co, fe, cr, mo, al, ti, nb, C, B, zr elements, and the mass percent (wt%) of the alloy components are as follows, co:9.3 to 15.5, fe:5.8 to 11.8, cr:15.5 to 17.8, mo:2.5 to 3.0, al:2.5 to 3.5, ti:2.0 to 3.0, nb:0.98 to 3.0, C:0.02 to 0.05, B: 0.005-0.015, zr:0.02 to 0.03, ni: the balance, and the atomic percentage ratio of (Ti+Nb)/Al is 0.5-1.
The density is lower than 8.0g/cm 3 The deformed high-strength high Wen Gaoshang alloy of (2) has a specific structural morphology: three different sizes of L1 2 The gamma 'phase particles are co-precipitated on the FCC-gamma matrix, the primary gamma' phase is mainly distributed in the grain boundary, the secondary and tertiary gamma 'phases are mainly distributed in the crystal, and the total volume percentage of the gamma' phase is 30-45%; after long-term aging at 750 ℃, the gamma' phase does not obviously coarsen and no harmful phase is generated, and the high-temperature structural stability is excellent.
The density is lower than 8.0g/cm 3 Typical properties of the deformed high strength high Wen Gaoshang alloy are: density of<8.0g/cm 3 Yield strength at room temperature>Elongation at room temperature of 1050MPa>18%, high temperature yield strength at 750 DEG C>800MPa。
A density lower than 8.0g/cm 3 The preparation method of the deformed high-strength high-Wen Gaoshang alloy comprises the following steps: firstly, weighing high-purity alloy materials according to mass percentage, and respectively adding the high-purity alloy materials into a vacuum arc melting furnace according to the melting point of elements, wherein Fe and C elements are close, at least repeatedly melting for 4 times, and starting an electromagnetic stirring system for 3-4 times to ensure that the components of an alloy ingot are uniform; secondly, homogenizing the alloy ingot by a muffle furnace for 1150-1200 ℃/2-4 h, and then performing multi-pass unidirectional cold rolling, wherein the single pressing amount is 0.1-1 mm, and the total pressing amount is 85-90%; finally, after solution treatment for 1020-1050 ℃/1h, adopting a two-stage aging process for 740-760 ℃/16-18h+640-660 ℃/24-26 h to obtain a final product.
The conception for realizing the technical scheme is as follows: novel density of less than 8.0g/cm using applicants' cluster composition design method 3 Is designed according to the composition of the deformation high-strength high-Wen Gaoshang alloy. The method forms a cluster type structural unit according to the interaction between elements, which is [ cluster type ]](connection atom) x I.e., a cluster of coordination polyhedrons centered on any one solute atom and surrounded by matrix atoms of the nearest neighbor shell, and x connecting atoms, the connecting atoms of the next nearest neighbor shell being used to match the average density of the alloy. For FCC-based alloy systems, the clusters are typically cuboctahedrons of coordination number CN12, and the number of linking atoms is typically x=3 to 5. The cluster component design method has been successfully applied to the design of various engineering alloys such as austenitic stainless steel for high temperature, low-elastic beta-Ti alloy, co-based superalloy and the like, and provides a new thought and method for the component design of high-performance engineering alloy.
According to the applicant's earlier work, in a ni—co based superalloy system, elements can be classified into Ni-like (Ni, fe, co), cr-like (Cr, mo, W) and Al-like (Al, ti, nb, ta) according to the element authors and the enthalpy of mixing between the element and the base element. The three elements entering the cluster are described below for simplicityPlain writingWherein (1)>The mixing enthalpy of the element and the matrix element is negative, the interaction is strong, and the element and the matrix element occupy the central atomic position preferentially; />The elements will preferentially occupy cluster positions, forming +.>Clusters, wherein the redundant content enters a connecting atom position; mixing enthalpy with matrix element is positive, interaction is weak +.>The elements occupy the connecting atomic positions. The novel deformation high Wen Gaoshang alloy cluster component is obtained by analyzing a plurality of deformation high-temperature alloys>
In the case of the new high Wen Gaoshang alloy,the elements mainly form a gamma prime coherent strengthening phase, and determine the content, precipitation temperature and precipitation rate of the gamma prime phase. Wherein Al element is a main element for forming gamma' phase, is beneficial to reducing alloy density, and can form a protective film on the surface of metal at high temperature, thereby improving the oxidation resistance and corrosion resistance of the alloy; the Nb element is slowly diffused, which is beneficial to reducing the formation rate and the precipitation temperature of gamma' -phase, but excessive Nb element content can cause serious segregation of alloy and form delta harmful phase; the Ti content is too high, so that eta harmful phase is formed, meanwhile, the dissolution temperature of gamma' phase is increased, and the hot working window is reduced. Precipitation of harmful phases can seriously affect the high-temperature stability of the gamma/gamma' coherent structure, and simultaneously ensure the low density and high density of the alloyThe strength is required, so that the content is limited, and the atomic percentage ratio of (Ti+Nb)/Al is required to be 0.5-1, so that no harmful phase is separated out, and the high-temperature tissue stability and excellent mechanical property are ensured. />The element plays a role in solid solution strengthening, and can play a role in corrosion resistance and oxidation resistance, and sigma harmful phase can be formed when Cr element is added excessively; the W element can improve the temperature bearing capacity of the alloy, but has high specific gravity and can greatly improve the density of the alloy; mo also reduces the notch sensitivity of the alloy, but excessive addition can lead to precipitation of deleterious phases such as topologically close-packed phases (TCP). />The element can improve the stability of the matrix, and meanwhile, the addition of a small amount of Co element can reduce the stacking fault energy of the matrix on the basis of ensuring the cost, so that the durability and creep resistance of the alloy are obviously improved; the addition of Fe element can reduce the alloy cost, but excessive addition can reduce the alloy strength and creep property. In addition, in order to refine grains and improve the binding force of grain boundaries, trace C, B, zr elements are required to be added, but excessive addition of the elements also affects the welding performance of the alloy, reduces the plasticity of the alloy, and easily generates boride carbide aggregation grain boundaries to affect the creep performance of the alloy. Thus, the final density was determined to be less than 8.0g/cm 3 The deformed high-strength high Wen Gaoshang alloy of (2) is as follows: ni- (9.3-15.5) Co- (5.8-11.8) Fe- (15.5-17.8) Cr- (2.5-3.0) Mo- (2.5-3.5) Al- (2.0-3.0) Ti- (0.98-3.0) Nb- (0.02-0.05) C- (0.005-0.015) B- (0.02-0.03) Zr.
The preparation method of the invention is as follows: firstly, weighing high-purity alloy materials according to mass percentage, and respectively adding the high-purity alloy materials into a vacuum arc melting furnace according to the melting point of elements, wherein Fe and C elements are close, at least repeatedly melting for 4 times, and starting an electromagnetic stirring system for 3-4 times to ensure that the components of an alloy ingot are uniform; secondly, homogenizing the alloy ingot by adopting a muffle furnace for 1150-1200 ℃/2-4 h, then carrying out multi-pass unidirectional cold rolling, wherein the single pressing amount is 0.1-1 mm, and the total pressing amount85-90%; finally, after solution treatment for 1020-1050 ℃/1h, adopting a two-stage aging process for 740-760 ℃/16-18h+640-660 ℃/24-26 h to obtain a final product. Detecting the alloy density using a densitometer (XS 64); using metallographic microscopes (OM), scanning Electron Microscopes (SEM), transmission Electron Microscopes (TEM) and X-ray diffractometers (XRD, cu K) α Radiation, λ= 0.15406 nm) to detect alloy structure and structure; hardness test of the alloy at 750 ℃ under different time aging is carried out by using an HVS-1000 Vickers hardness tester; and (3) testing the tensile mechanical properties at the temperature of 750 ℃ by using a UTM5504 electronic universal tensile testing machine. It was thus determined that the present invention has the above-mentioned density of less than 8.0g/cm 3 Is a high strength Wen Gaoshang alloy. The alloy comprises the following components in percentage by mass: co:9.3 to 15.5, fe:5.8 to 11.8, cr:15.5 to 17.8, mo:2.5 to 3.0, al:2.5 to 3.5, ti:2.0 to 3.0, nb: 0.98-3.0, C:0.02 to 0.05, B: 0.005-0.015, zr:0.02 to 0.03, ni: the balance, and the atomic percentage ratio of (Ti+Nb)/Al is 0.5-1. The organization and performance indexes of the material are as follows: alloy density<8.0g/cm 3 The method comprises the steps of carrying out a first treatment on the surface of the Room temperature yield strength sigma s >1050MPa, tensile strength sigma b >1450MPa, elongation delta>18%; high temperature yield strength sigma at 750 DEG C s >800MPa; after two-stage aging, three L1 with different sizes 2 The gamma 'phase particles are co-precipitated on the gamma matrix, the primary gamma' phase is mainly distributed on the grain boundary, the secondary and tertiary gamma 'phases are mainly distributed in the grain, and the total volume percentage of the gamma' phase is 30-45%; after long-term aging at 750 ℃/500h, gamma 'particles are not obviously coarsened and no harmful phase is generated, the gamma/gamma' coherent structure is stable, and the alloy hardness is stable at 410-510 kgf.mm -2 Between them.
Compared with the prior art, the invention has the beneficial effects that:
(1) The invention designs and develops a deformation high-strength high-Wen Gaoshang alloy with lower density according to a cluster composition method which is developed by the applicant. Compared with the prior deformed high-temperature alloy, the alloy density of the invention<8.0g/cm 3 Far less than the current typical wrought superalloys, such as the In718 alloy (8.24 g/cm 3 ) In718Plus alloy (8.36 g/cm) 3 ) And U720Li alloy (8.14 g/cm 3 ) And the like, and meanwhile, a certain amount of Fe element is contained, so that the preparation process is simple, and the material cost is reduced;
(2) The density of the series is lower than 8.0g/cm 3 The microstructure of the deformed high-strength high Wen Gaoshang alloy is shown that gamma 'particles with three sizes are co-precipitated on a gamma matrix, and primary gamma' phases are mainly distributed on a crystal boundary and can be used for pinning the crystal boundary and refining grains; the secondary and tertiary gamma ' phases are mainly distributed in the crystal, wherein the tertiary fine gamma ' phases are uniformly distributed on the matrix, and the secondary and tertiary fine gamma ' phases mainly take a dislocation shearing mechanism in the deformation process and play a main role in alloy precipitation strengthening; the total volume percentage of the gamma '-phase is 30-45%, and the alloy contains Nb element, can reduce the precipitation temperature and the precipitation rate of the gamma' -phase, enlarge the hot working window of the alloy, is beneficial to alloy processing, and ensures that the alloy has room temperature plasticity>18％；
(3) Under the condition that high temperature elements such as W, ta and the like are not present, the gamma' phase is not obviously coarsened and no harmful phase is generated after long-term aging at 750 ℃, and the alloy has excellent high-temperature tissue stability; and the high temperature yield strength of the series alloy at 750 ℃ is more than 800MPa.
Drawings
Fig. 1 is an SEM tissue morphology diagram of the alloy prepared in example 1, three sizes of gamma ' particles are co-precipitated on the gamma matrix, large size gamma ' particles are precipitated at the grain boundaries, and larger and smaller size gamma ' particles are precipitated in the crystals.
Detailed Description
The following describes specific embodiments of the present invention in detail with reference to the drawings.
Example 1:
ni-15.34Co-5.82Fe-15.97Cr-2.50Mo-2.53Al-2.99Ti-2.90Nb-0.03C-0.015B-0.03Zr (wt.%) alloy
Step one: alloy preparation
Adopting high-purity raw materials, mixing 100g of raw materials according to mass percent, putting into a vacuum arc furnace, wherein Fe and C elements are close, repeatedly smelting the raw materials for 5 times under the argon atmosphere, and simultaneously starting an electromagnetic stirring system for 4 times during smelting to obtain alloy ingots with uniform components. The alloy ingot is subjected to homogenization treatment of 1200 ℃/2h by a muffle furnace. And then carrying out multi-pass cold rolling, wherein the pressing amount of each pass of rolling is not more than 0.5mm, the total deformation amount is about 85%, and a plate sample with the thickness of about 2mm is obtained. Then carrying out solid solution treatment at 1050 ℃/1h, and then carrying out two-stage aging treatment at 760 ℃/16h+650 ℃/24h.
Step two: alloy density, texture and mechanical property test
Alloy density was measured using densitometer and found to be 7.98g/cm 3 The method comprises the steps of carrying out a first treatment on the surface of the The structure and structure of the alloy after the stabilization treatment are detected by OM, SEM and XRD, and the result shows that the gamma ' particles with different sizes of the alloy are co-precipitated on a gamma matrix, which is shown in figure 1, and the gamma ' particles can stably exist for a long time at 750 ℃, the size of the gamma ' particles is basically unchanged after aging for 500 hours, and the size of the primary gamma ' particles is basically the same as that of the gamma ' particles>500nm, the secondary gamma ' size is 270nm, the tertiary gamma ' size is 80nm, the volume percentage is stabilized at 42%, the gamma/gamma ' coherent structure is stable, and other harmful phases are not separated out; hardness testing was performed using a vickers hardness tester, and after two-stage aging and at 750 ℃ for 100h, 200h, and 500h, respectively, the hardness hv=500±10kgf·mm -2 Is basically unchanged; tensile property data at room temperature and 750 ℃ were measured using an MTS universal tensile tester: room temperature yield strength sigma s =1346 MPa, tensile strength σ b =1629 MPa, elongation after break δ=18.5%; high temperature yield strength sigma at 750 DEG C s ＝1043MPa。
Example 2:
ni-15.47Co-5.87Fe-17.20Cr-2.52Mo-2.55Al-3.0Ti-0.98Nb-0.02C-0.01B-0.025Zr (wt.%) alloy
Step one: alloy preparation
Adopting high-purity raw materials, mixing 100g of raw materials according to mass percent, putting into a vacuum arc furnace, wherein Fe and C elements are close, repeatedly smelting the raw materials for 4 times under the argon atmosphere, and simultaneously starting an electromagnetic stirring system for 3 times during smelting to obtain alloy ingots with uniform components. The alloy ingot is subjected to homogenization treatment of 1200 ℃/4h by a muffle furnace. And then carrying out multi-pass cold rolling, wherein the pressing amount of each pass of rolling is not more than 0.2mm, the total deformation amount is about 85%, and a plate sample with the thickness of about 2mm is obtained. Then carrying out solid solution treatment at 1050 ℃/1.5h, and then carrying out two-stage aging treatment at 750 ℃/18h+660 ℃/26h.
Step two: alloy density, texture and mechanical property test
Alloy density was measured using densitometer and found to be 7.93g/cm 3 The method comprises the steps of carrying out a first treatment on the surface of the The structure and structure of the stabilized alloy are detected by OM, SEM and XRD, and the result shows that the gamma ' particles with different sizes of the alloy are co-precipitated on a gamma matrix, which is similar to the method in the example 1, and the gamma ' particles can stably exist for a long time at 750 ℃, the size of the gamma ' particles is basically unchanged after aging for 500 hours, and the size of the primary gamma ' particles is basically the same as that of the gamma ' particles>500nm, the secondary gamma ' size is 270nm, the tertiary gamma ' size is 70nm, the volume percentage is stabilized at 38%, the gamma/gamma ' coherent structure is stable, and other harmful phases are not separated out; hardness testing was performed using a vickers hardness tester, and after two-stage aging and at 750 ℃ for 100h, 200h, and 500h, respectively, the hardness hv=475±8kgf·mm -2 Is basically unchanged; tensile property data at room temperature and 750 ℃ were measured using an MTS universal tensile tester: room temperature yield strength sigma s =1151mpa, tensile strength σ b =1505 MPa, elongation after break δ=18.7%; high temperature yield strength sigma at 750 DEG C s ＝884MPa。
Example 3:
ni-12.41Co-11.76Fe-17.80Cr-2.53Mo-2.56Al-2.52Ti-0.98Nb-0.03C-0.005B-0.02Zr (wt.%) alloy
Step one: alloy preparation
Adopting high-purity raw materials, mixing 100g of raw materials according to mass percent, putting into a vacuum arc furnace, wherein Fe and C elements are close, repeatedly smelting the raw materials for 4 times under the argon atmosphere, and simultaneously starting an electromagnetic stirring system for 3 times during smelting to obtain alloy ingots with uniform components. The alloy ingot is homogenized by a muffle furnace at 1150 ℃/2h and a heating rate of 10 ℃ per minute. And then carrying out multi-pass cold rolling, wherein the pressing amount of each pass of the cold rolling is not more than 0.5mm, the total deformation amount is about 90%, and a plate sample with the thickness of about 1.6mm is obtained. Then carrying out 1020 ℃/1h solid solution treatment, and then carrying out two-stage aging treatment, 740 ℃/18h+640 ℃/26h.
Step two: alloy density, texture and mechanical property test
Alloy density was measured using densitometer and found to be 7.87g/cm 3 The method comprises the steps of carrying out a first treatment on the surface of the The structure and structure of the stabilized alloy are detected by OM, SEM and XRD, and the result shows that the gamma ' particles with different sizes of the alloy are co-precipitated on a gamma matrix, which is similar to the method in the example 1, and the gamma ' particles can stably exist for a long time at 750 ℃, the size of the gamma ' particles is basically unchanged after aging for 500 hours, and the size of the primary gamma ' particles is basically the same as that of the gamma ' particles>500nm, the secondary gamma ' dimension to 260nm, the tertiary gamma ' dimension to 65nm, the volume percentage to be stabilized at 33%, the gamma/gamma ' coherent structure to be stable, and no other harmful phase to be separated out; hardness testing was performed using a Vickers hardness tester, after two-stage aging and at 750℃for 100h, 200h, 500h, respectively, with hardness HV=425.+ -. 14 kgf.mm -2 Is basically unchanged; tensile property data at room temperature and 750 ℃ were measured using an MTS universal tensile tester: room temperature yield strength sigma s =1057 MPa, tensile strength σ b 1453MPa, elongation after break δ=21.1%; high temperature yield strength sigma at 750 DEG C s ＝820MPa。
Example 4:
ni-9.30Co-8.82Fe-15.87Cr-3.00Mo-3.41Al-2.02Ti-1.96Nb-0.02C-0.015B-0.02Zr (wt.%) alloy
Step one: alloy preparation
Adopting high-purity raw materials, mixing 100g of raw materials according to mass percent, putting into a vacuum arc furnace, wherein Fe and C elements are close, repeatedly smelting the raw materials for 5 times under the argon atmosphere, and simultaneously starting an electromagnetic stirring system for 3 times during smelting to obtain alloy ingots with uniform components. The alloy ingot is subjected to homogenization treatment of 1200 ℃/4h by a muffle furnace. And then carrying out multi-pass cold rolling, wherein the pressing amount of each pass of rolling is not more than 0.5mm, the total deformation amount is about 85%, and a plate sample with the thickness of about 2mm is obtained. Then carrying out solid solution treatment at 1050 ℃/1h, and then carrying out two-stage aging treatment at 760 ℃/16h+650 ℃/24h.
Step two: alloy density, texture and mechanical property test
Alloy density was measured using densitometer and found to be 7.90g/cm 3 The method comprises the steps of carrying out a first treatment on the surface of the The structure and structure of the alloy after stabilization treatment are detected by OM, SEM and XRD, and the result shows that the alloy containsThe gamma 'particles with different sizes of gold are precipitated on the gamma matrix in a coherent manner, similar to example 1, and can exist stably for a long time at 750 ℃, the size of the gamma' particles is basically unchanged after aging for 500 hours, and the size of the primary gamma 'particles is basically the same as that of the gamma' particles>500nm, the secondary gamma ' dimension is 275nm, the tertiary gamma ' dimension is 82nm, the volume percentage is stabilized at 35%, the gamma/gamma ' coherent structure is stable, and other harmful phases are not separated out; hardness testing was performed using a Vickers hardness tester, after two-stage aging and at 750℃for 100h, 200h, 500h, respectively, with hardness HV=479.+ -. 17 kgf.mm -2 Is basically unchanged; tensile property data at room temperature and 750 ℃ were measured using an MTS universal tensile tester: room temperature yield strength sigma s =1185 MPa, tensile strength σ b 1535MPa, elongation after break δ=19.5%; high temperature yield strength sigma at 750 DEG C s ＝897MPa。
Example 5:
ni-9.3Co-8.82Fe-15.5Cr-3.0Mo-3.5Al-2.52Ti-3.0Nb-0.02C-0.005B-0.02Zr (wt.%) alloy
Step one: alloy preparation
Adopting high-purity raw materials, mixing 100g of raw materials according to mass percent, putting into a vacuum arc furnace, wherein Fe and C elements are close, repeatedly smelting the raw materials for 5 times under the argon atmosphere, and simultaneously starting an electromagnetic stirring system for 4 times during smelting to obtain alloy ingots with uniform components. The alloy ingot is subjected to homogenization treatment of 1200 ℃/4h by a muffle furnace. And then carrying out multi-pass cold rolling, wherein the pressing amount of each pass of rolling is not more than 0.5mm, the total deformation amount is about 85%, and a plate sample with the thickness of about 2mm is obtained. Then carrying out solid solution treatment at 1050 ℃/1h, and then carrying out two-stage aging treatment at 760 ℃/16h+650 ℃/24h.
Step two: alloy density, texture and mechanical property test
Alloy density was measured using densitometer and found to be 7.93g/cm 3 The method comprises the steps of carrying out a first treatment on the surface of the The structure and structure of the stabilized alloy are detected by OM, SEM and XRD, and the result shows that the gamma ' particles with different sizes of the alloy are co-precipitated on a gamma matrix, which is similar to the method in the example 1, and the gamma ' particles can stably exist for a long time at 750 ℃, the size of the gamma ' particles is basically unchanged after aging for 500 hours, and the size of the primary gamma ' particles is basically the same as that of the gamma ' particles>500nm, the secondary gamma ' dimension to 250nm, the tertiary gamma ' dimension to 85nm, the volume percentage is stabilized at 45%, the gamma/gamma ' coherent structure is stable, and other harmful phases are not separated out; hardness testing was performed using a Vickers hardness tester, after two-stage aging and at 750℃for 100h, 200h, 500h, respectively, with hardness HV=523+ -8 kgf.mm -2 Is basically unchanged; tensile property data at room temperature and 750 ℃ were measured using an MTS universal tensile tester: room temperature yield strength sigma s =1347 MPa, tensile strength σ b =1685 MPa, elongation after break δ=18.2%; high temperature yield strength sigma at 750 DEG C s ＝1085MPa。
The examples described above represent only embodiments of the invention and are not to be understood as limiting the scope of the patent of the invention, it being pointed out that several variants and modifications may be made by those skilled in the art without departing from the concept of the invention, which fall within the scope of protection of the invention.
Claims (3)
1. A density lower than 8.0g/cm 3 The deformed high-strength high-Wen Gaoshang alloy is characterized by having a density of less than 8.0g/cm 3 The deformation high-strength high Wen Gaoshang alloy of (2) comprises Ni, co, fe, cr, mo, al, ti, nb, C, B, zr elements, wherein the alloy comprises the following components in percentage by mass: 9.3 to 15.5, fe:5.8 to 11.8, cr:15.5 to 17.8, mo:2.5 to 3.0, al:2.5 to 3.5, ti:2.0 to 3.0, nb: 0.98-3.0, C:0.02 to 0.05, B: 0.005-0.015, zr:0.02 to 0.03, ni: the balance, and the atomic percentage ratio of (Ti+Nb)/Al is 0.5-1;
the alloy has a specific structure morphology: three different sizes of L1 2 The gamma 'phase particles are co-precipitated on the FCC-gamma matrix, the primary gamma' phase is mainly distributed on the grain boundary, the secondary and tertiary gamma 'phases are mainly distributed in the crystal, and the total volume percentage of the gamma' phase is 30-45%; no significant coarsening and no detrimental phase formation after long-term aging at 750 ℃.
2. A density of less than 8.0g/cm according to claim 1 3 High strength and high deformationWen Gaoshang alloy, characterized in that the alloy has typical properties: density of<8.0g/cm 3 Yield strength at room temperature>Elongation at room temperature of 1050MPa>18%, high temperature yield strength at 750 DEG C>800MPa。
3. A density according to claim 1 or 2 of less than 8.0g/cm 3 The preparation method of the deformed high-strength high-Wen Gaoshang alloy is characterized by comprising the following steps of:
firstly, weighing high-purity alloy materials according to mass percentage, respectively adding the alloy materials into a vacuum arc melting furnace according to the melting point of elements, wherein Fe and C are close to each other, and repeatedly melting for at least 4 times, and starting an electromagnetic stirring system for 3-4 times during the process to ensure that the components of alloy ingots are uniform; secondly, homogenizing the alloy ingot by a muffle furnace for 1150-1200 ℃/2-4 h, and then performing multi-pass unidirectional cold rolling, wherein the single pressing amount is 0.1-1 mm, and the total pressing amount is 85-90%; finally, after solution treatment for 1020-1050 ℃/1h, adopting a two-stage aging process for 740-760 ℃/16-18h+640-660 ℃/24-26 h to obtain a final product.
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| CN102625856A (en) * | 2009-08-20 | 2012-08-01 | 奥贝尔&杜瓦尔公司 | Nickel-based superalloy and parts made from said superalloy |
| CN106661674A (en) * | 2014-09-29 | 2017-05-10 | 日立金属株式会社 | Ni based superheat-resistant alloy |
| CN111139391A (en) * | 2020-01-10 | 2020-05-12 | 合肥工业大学 | Precipitation strengthening type high-entropy alloy and preparation process thereof |
| CN113528921A (en) * | 2021-06-23 | 2021-10-22 | 沈阳航空航天大学 | C-containing high-performance multi-principal-element high-entropy alloy and preparation method thereof |
| CN114438391A (en) * | 2022-01-25 | 2022-05-06 | 中南大学 | Precipitation strengthening high-entropy alloy component design and preparation method based on diffusion multi-element technology |
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| CN102625856A (en) * | 2009-08-20 | 2012-08-01 | 奥贝尔&杜瓦尔公司 | Nickel-based superalloy and parts made from said superalloy |
| CN106661674A (en) * | 2014-09-29 | 2017-05-10 | 日立金属株式会社 | Ni based superheat-resistant alloy |
| CN111139391A (en) * | 2020-01-10 | 2020-05-12 | 合肥工业大学 | Precipitation strengthening type high-entropy alloy and preparation process thereof |
| CN113528921A (en) * | 2021-06-23 | 2021-10-22 | 沈阳航空航天大学 | C-containing high-performance multi-principal-element high-entropy alloy and preparation method thereof |
| CN114438391A (en) * | 2022-01-25 | 2022-05-06 | 中南大学 | Precipitation strengthening high-entropy alloy component design and preparation method based on diffusion multi-element technology |
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