CN110468323B - High-strength ductile multi-principal-element alloy and preparation method thereof - Google Patents
High-strength ductile multi-principal-element alloy and preparation method thereof Download PDFInfo
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Abstract
The invention relates to the preparation of alloy materialThe technical field, in particular to a multi-principal-element alloy with high ductility and toughness, which has the following structure: al (Al)0.5Cr0.9FeNi2.5TiNx(x is 0.0, 0.2, 0.4, 0.6, 0.8, 1.0). The strongest diffraction peak of the alloy provided by the invention firstly moves leftwards and then rightwards, the lattice constant firstly increases and then decreases, but the phase structure is kept unchanged, a BCC phase begins to appear in the alloy, and a lath-shaped structure and nano particles appear in the BCC. After the TIN is added, the alloy hardness is improved by nearly 3 times; the wear resistance is improved by nearly 1 time. The compressive strength of the master alloy is 925MPa, the alloy is not fractured, the plastic deformation of the alloy is large, and after TiN is added, the fracture strength of the alloy is improved to 2006MPa and the fracture strain is about 18%.
Description
Technical Field
The invention relates to the technical field of alloy material preparation, in particular to a high-strength ductility and toughness multi-principal-element alloy and a preparation method thereof.
Background
With the rapid development of the recent heavy industry, materials become more and more the first problem limiting the development of the heavy industry, the performance of common alloys can not meet the requirements of key parts, and people are eagerly seeking a novel alloy meeting special requirements. The traditional alloy design concept considers that the more components in the alloy, the easier it is to form complex intermetallic compounds, and the more difficult it is to analyze. Yeh first proposed a design concept of multi-component alloy in 2004, that is, multi-principal components do not cause brittle phases such as various complex intermetallic compounds to be formed in the alloy, and on the contrary, help the alloy to form a stable solid solution. The idea breaks through the traditional alloy design mode and improves the understanding of people on the alloy to a new height.
Wu has studied the influence of different Al contents on the microstructure and the adhesive wear performance of the AlxCoCrCuFeNi high-entropy alloy, and the result shows that the BCC phase relative quantity and the wear resistance are greatly increased along with the increase of the Al content. Anil Kumar vs alcoccrfenisixThe studies of (2) found that Si element promotes the generation of BCC phase and hard phase. Hus was in 2004 at CuCoNiCrAl0.5The Fe high-entropy alloy is introduced with non-metallic boron (B) element, which is found to remarkably improve the wear resistance of the FCC alloy. However, the design of equimolar atomic ratios theoretically limits the formation of some toughness-strengthening phases. Therefore, Liang developed an isoatomic system Al for obtaining a toughness-enhancing phase0.5Cr0.9FeNi2.5V0.2The system increases the Ni/Al ratio by increasing the Ni content. While the domestic scholars LiDepeng adopt high-entropy alloy Al with non-equal molar ratio0.2Co1.5CrFe1.2Ni1.5TiC0.4To study the effect of ceramic phase TiC on the alloy. These researchers studied the influence of the metallic addition phase and the nonmetallic addition phase on the performance structure of the multi-principal-element alloy in order to promote the formation of the BCC system, but no researchers have yet studied a low-cost, high-strength, ductile and multi-principal-element alloy.
Disclosure of Invention
In order to overcome the defects of the technical problems, the invention provides a multi-principal-element alloy with high ductility and toughness, which has the advantages of low cost, excellent strength and hardness and excellent ductility and toughness performance.
The technical scheme for solving the technical problems is as follows:
the invention designs a high-strength ductile multi-principal-element alloy, which has the following structure: in terms of mole ratio, Al0.5Cr0.9FeNi2.5TiNx(x＝0.2、0.4、0.6、0.8、1.0)。
Preferably: in terms of mole ratio, Al0.5Cr0.9FeNi2.5TiN0.8。
The invention also provides a preparation method of the multi-principal-element alloy, which comprises the following steps:
1) using electronic balancesAccurately weighing smelting raw materials, and respectively weighing Al, Cr, Fe, Ni and TiN simple substance blocks with the purity higher than 99.9 percent according to the mole fraction of Al0.5Cr0.9FeNi2.5TiNxPreparing x is 0.2, 0.4, 0.6, 0.8 and 1.0; the percentage contents are all atomic percentage.
In-system TiNxAs a ceramic phase, the addition of the ceramic phase can directly improve the hardness and strength of the alloy of the system; wherein, Ti and N can participate in chemical reaction of other elements to further improve the strength of the alloy.
2) Vacuum arc melting: vacuumizing the electric arc furnace to the vacuum degree of (4.5-4.8) x 10-3Pa, then arc melting under the atmosphere of high-purity argon at the current of 150A-300A to prepare Al0.5Cr0.9FeNi2.5TiNx(x ═ 0.2, 0.4, 0.6, 0.8, 1.0) alloy ingots, each about 30 g; in the preparation process, the ingot is inverted and remelted for at least 5 times, so that the raw materials are fully dissolved and uniformly distributed to improve the chemical uniformity. The purity of the high-purity argon is more than 99.999 percent, and the high-purity argon is filled until the vacuum degree is-0.05 MPa.
The invention has the beneficial effects that:
the high-strength ductility and toughness multi-principal-element alloy Al provided by the invention0.5Cr0.9FeNi2.5TiNx(x is 0.2, 0.4, 0.6, 0.8, 1.0) the phase structure of the alloy is Fe-Ni based FCC solid solution phase + Ni3[Al，Ti]BCC phase and TIN ceramic phase such as TiCr, AlCr and NiAl. After TiN is added, the strongest diffraction peak moves to the left and then to the right, the lattice constant increases and then decreases, but the phase structure is kept unchanged, the BCC phase begins to appear in the alloy, and the lath-shaped structure and the nano particles appear in the BCC. After the TIN is added, the alloy hardness is improved by nearly 3 times; the wear resistance is improved by nearly 1 time. The compressive strength of the master alloy is 925MPa, the alloy is not fractured, the plastic deformation of the alloy is large, and after TiN is added, the fracture strength of the alloy is improved to 2006MPa and the fracture strain is about 18%.
The high-strength ductility and toughness multi-principal-element alloy Al provided by the invention0.5Cr0.9FeNi2.5TiNx(x＝0.2. 0.4, 0.6, 0.8, 1.0) alloy is non-molar ratio Al0.5Cr0.9FeNi2.5Its high Ni/Al ratio in combination with the additive elements may promote the formation of the BCC phase.
Drawings
The present invention will be described in further detail with reference to the accompanying drawings and specific embodiments.
FIG. 1 is an X-ray diffraction pattern of the present invention;
FIG. 2 is an enlarged view of a portion of FIG. 1;
FIG. 3 shows the microscopic morphology of the field emission electron microscope of the present invention, wherein (a, c, e, g, i, k) is Al0.5Cr0.9FeNi2.5TiNx(x is 0.0, 0.2, 0.4, 0.6, 0.8, 1.0)2 k-fold pattern, (b, d, f, h, j, l) is Al0.5Cr0.9FeNi2.5TiNx(x ═ 0.0, 0.2, 0.4, 0.6, 0.8, 1.0) of a 10 k-fold topography;
FIG. 4 shows Al in the present invention0.5Cr0.9FeNi2.5TiN0.8The element distribution diagram of the alloy, wherein (a, b, c, d, e, f) are the element distribution diagrams of Al, Cr, Fe, N, Ni and Ti respectively;
FIG. 5 is a 30kx profile of a thermal field emission electron microscope of the present invention, wherein (a, b, c, d, e, f) are Al0.5Cr0.9FeNi2.5TiNx(x ═ 0.0, 0.2, 0.4, 0.6, 0.8, 1.0) morphology;
FIG. 6 is a graph of the change in Vickers hardness of the present invention;
FIG. 7 is a stress-strain plot of the present invention;
FIG. 8 is a surface topography after frictional wear, where the plots (a, c, e, g, i, k) are for Al0.5Cr0.9FeNi2.5TiNx(x is 0.0, 0.2, 0.4, 0.6, 0.8, 1.0)200x topography, plot (b, d, f, h, j, l) is Al0.5Cr0.9FeNi2.5TiNx(x ═ 0.0, 0.2, 0.4, 0.6, 0.8, 1.0)500x topography;
FIG. 9 is a graph showing the friction coefficient of each alloy component.
Detailed Description
Example (b):
1) accurately weighing smelting raw materials by using an electronic balance, and respectively weighing Al, Cr, Fe, Ni and TiN simple substance blocks with the purity higher than 99.9 percent according to the mole fraction of Al0.5Cr0.9FeNi2.5TiNx(x is 0.0, 0.2, 0.4, 0.6, 0.8, 1.0);
2) vacuum arc melting: vacuumizing the electric arc furnace to the vacuum degree of (4.5-4.8) x 10-3Pa, then filling high-purity argon into the furnace under the atmosphere of high-purity argon with the purity of more than 99.999 percent until the vacuum degree is-0.05 Mpa and the current is 150A-300A, and carrying out arc melting to prepare Al0.5Cr0.9FeNi2.5TiNxAnd (x ═ 0.0, 0.2, 0.4, 0.6, 0.8, 1.0) alloy ingots, each of which was about 30 g. During the preparation, the ingot is inverted and remelted at least 5 times to improve chemical homogeneity.
Pure metals of Al, Cr, Fe and Ni and TiN particles (purity)>99 percent) are subjected to electric arc melting in the atmosphere of high-purity argon to prepare Al0.5Cr0.9FeNi2.5TiNx(x is 0.0, 0.2, 0.4, 0.6, 0.8, 1.0) and about 30 g. During the preparation, the ingot is inverted and remelted at least 5 times to improve chemical homogeneity. The molar ratio of the components of the alloy is indicated by subscripts, and the molar ratio is respectively corresponding to Al with different components0.5Cr0.9FeNi2.5TiNxThe multicomponent alloy is numbered according to the sequence of TiN content from low to high, x is 0.0, 0.2, 0.4, 0.6, 0.8 and 1.0. The ingot was cut by a wire electric discharge machine to obtain a sample having a standard size of 14mm x 7mm x 4mm and a cylinder having a diameter of 3mm and a height of 6 mm. Prior to the experiment, the ingot samples were sanded and polished, followed by electropolishing using 10% perchloric acid + 90% glacial acetic acid. In order to obtain the phase composition of the sample, an X-ray diffractometer is adopted to carry out an X-ray diffraction experiment with the speed of 8 degrees/min and the range of 20 degrees to 90 degrees on the sample. The morphology and the structure of the ingot sample are observed under a field emission electron microscope (FEG-SEM, GeminiSEM), and the chemical composition of the ingot is analyzed by using an energy dispersion spectroscopy (EDS, Oxford Tools, Oxford, England) equipped with a scanning electron microscope. Digital display of small load by HVS-5Vickers hardness tester, separately measuring Al0.5Cr0.9FeNi2.5TiNx(x is 0.0, 0.2, 0.4, 0.6, 0.8 and 1.0), the hardness of the composite alloy sample is set to be 1000g, the time interval T is 15s, the composite alloy sample is measured by using a 40-time eyepiece, three points are selected at each position, and the hardness of the position is averaged to increase the accuracy of the experimental result. The compression experiment was performed on each cylindrical sample using a universal tester, each set of compressions was repeated three times, and the average was taken, where the strain rate was 10-3s-1. The test was carried out by subjecting each sample to a reciprocating frictional wear test using a multifunctional tester (MFT-4000), pretreating the surface of the sample with 2000# sandpaper before the test, selecting SiN pellets with a friction head diameter of 3mm, at a speed of 50mm/min, for a time of 30min, at a length of 10mm, and under a load of 10N.
FIG. 1 shows Al0.5Cr0.9FeNi2.5TiNxAs a result of XRD diffraction analysis of the multi-element alloy, it was found that Al containing no TiN and a small amount of TiN (i.e., x is 0.2 or 0.4) was added0.5Cr0.9FeNi2.5TiNxThe multi-principal element alloy only contains an FCC single phase. Wherein the FCC phase is mainly [ Fe-Ni ]]The solid solution has the advantages of soft structure, small hardness and good plasticity. However, as the content of TiN increases, a BCC phase with high hardness begins to appear when x is 0.6, and it can be presumed from the energy spectrum that the phase composition of the BCC phase is mainly Ni3[Al，Ti]Phase and small amount of TiCr, AlCr and NiAl phases. It is not difficult to find that the intensity of BCC diffraction peak increases gradually from zero to some extent with the increase of TiN content, and the FCC peak intensity decreases gradually. Many kinds of complex intermetallic compounds are not generated among the small number of diffraction peak types.
Because of more TiN, a saturated or supersaturated solid solution tends to be formed, the solid solubility of the alloy elements is greatly improved, and the solid solution strengthening effect is greatly improved. The solid solubility of this solid solution form gradually increases with the continuous addition of TiN element. Therefore, as the content of TiN element increases, Al0.5Cr0.9FeNi2.5TiNxThe solid solution strengthening effect of the multi-principal-element alloy structure is gradually increased. The FCC X-ray diffraction intensity subsequently started when X was 0.6Gradually decreases. This is probably due to the increased TiN content, which causes FCC lattice distortion.
As a result of calculation, since lattice distortion constants when x is 0.0, 0.2, 0.4, 0.6, 0.8, and 1.0 are 3.6025, 3.6033, 3.6088, 3.6100, 3.6835, and 3.6062, respectively, the addition of TiN causes lattice distortion of the FCC phase, and the diffraction peak shifts to the left. As shown in fig. 2, the degree of lattice distortion becomes larger as the TiN content increases, and reaches a maximum value at x of 0.8. The phenomenon of lattice distortion occurs because the balance between atoms is destroyed, which leads to lattice distortion, that is, when the phenomenon of lattice distortion occurs, the atoms leave their original equilibrium positions, which leads to the increase of potential energy, the microscopic stress of the material is increased, which in turn hinders the slip and deformation of dislocation, that is, the increase of lattice distortion constant increases the difficulty of dislocation movement. Therefore, made of Al0.5Cr0.9FeNi2.5TiNxThe XRD diffraction analysis result of the multi-principal element alloy can obtain that: as the TiN content increases, the degree of lattice distortion of the alloy becomes larger and reaches a maximum at x of 0.8.
FIG. 3 is an electron micrograph, and it can be seen from the energy spectrum and XRD of FIG. 4 that A is FCC matrix [ Fe, Ni ] solid solution, B is Ni3[ Al, Ti ] phase and AlCr, NiAl phase belong to BCC structure, and C is TiN belongs to BCC structure. When x is 0, it can be seen that part of the grain boundary disappears, the grain boundary becomes larger as TiN is added, and the Ni3[ Al, Ti ] phase appears and gradually increases, and is dispersed more dispersedly, while TiN which does not participate in the reaction is also included between FCC and BCC. The lath structure begins to gradually appear in the BCC phase, the content is more and more, and the morphology containing lamellar layers is mainly a Cr-rich phase.
At the beginning of the TIN addition, the presence of the BCC phase in the shape of broken petals is relatively small because the BCC phase is mainly the Ni3[ Al, Ti ] phase, but the Ti content in the starting phase is relatively limited, and even if the BCC phase is completely reacted, the BCC phase is not enough to share too much Ni, and the reason is that the lath-shaped Cr-rich phase is relatively small. However, with the increase of the dosage, the influence on the FCC phase is more and more found, enough Ti participates in the reaction, the BCC structure is gradually increased, the Cr element can be combined with the BCC structure to form a lath-shaped Cr-rich structure, the Cr element is staggered in the BCC, the Cr element has certain affinity with elements such as Ti, Al and the like, the Cr element is increased along with the addition amount, the internal structure of the FCC is influenced, part of the Cr element is attracted, and the appearance of the alloy structure is greatly influenced. Meanwhile, more and more TiN which does not participate in the reaction exists at the boundary of FCC and BCC in the form of inclusion, which has great influence on the mechanical property of the alloy, and is mainly reflected on the influence of high-hardness TiN ceramic on the hardness of the alloy, so that the TiN ceramic can be multiplied.
When x is larger than or equal to 0.6, we find that in the BCC phase, a fine nano phase begins to be attached and precipitated on the lath-shaped tissue in a high-power (30 k-power) electron microscope (as shown in FIG. 5), and the size is about 10-20nm, but the content is relatively small. And when the TiN content is highest (fig. f), the BCC phase is filled with the TiN. The main reason for the appearance of nano particles is that the addition of TiN promotes BCC to grow without time to form nuclei, and BCC which does not grow is in the form of fine nano particles and is uniformly filled in the BCC. As can be seen from the graph f, the nanoparticles are almost spread inside the BCC, and it can be said that controlling the addition of TiN is a method for controlling the formation of the nano-phase.
FIG. 6 is Al0.5Cr0.9FeNi2.5TiNxThe microhardness of the multi-principal element alloy randomly tested reflects a histogram. The average hardness of the alloy at x 0.0, 0.2, 0.4, 0.6, 0.8 and 1.0 is 223.93Hv, 380.91Hv, 517.66Hv, 563.08Hv, 594.29Hv and 657.74Hv, respectively, and it is very obvious that the average hardness of the alloy rapidly increases with the increase in TiN content, which is significantly higher than the matrix hardness, and the average hardness of the alloy at x 1 is 2.94 times the average hardness of the alloy at x 0, and the hardness is very low at x 0, which is caused by the fact that the crystal grains are too large, the fine grain strengthening mechanism is lacking, and there is not enough grain boundaries to hinder the slip of dislocations. The atomic radii of Fe, Cr, Ni, Al, Ti and N are respectively 124pm, 121pm, 124pm, 143pm, 145pm and 80pm, and the atomic radius of Ti is the largest among six elements, and is added into the alloy system, so that crystal lattices are distorted to form lattice distortionThe hardness of the alloy is improved, i.e., solid solution strengthening.
The FCC phase is soft, but the BCC phase appears to increase the hardness, and the hardness gradually increases with the increase of the content of BCC. TIN, which is between FCC and BCC, is also one of the main causes of hardness increase, so the solid solution strengthening effect of TIN is probably the most important cause of hardness increase. In addition, the appearance of a nano-phase that has not been nucleated in BCC enhances precipitation strengthening and contributes to an increase in hardness.
FIG. 7 shows Al0.5Cr0.9FeNi2.5TiNxStress-strain curve of multi-principal element alloy under different TiN content. It is evident that Al increases with the TiN content0.5Cr0.9FeNi2.5TiNxThe fracture strength of the multi-element alloy is obviously improved, the fracture strength of the alloy reaches the maximum value of 2006MPa when x is 0.8, and the strain is shown in the specification that when x is 0.8, Al0.5Cr0.9FeNi2.5TiNxThe strength of the multi-principal element alloy is highest. At 0.0, 0.2, the strain was 50% and did not break, indicating that the matrix was very well shaped, mainly [ Fe, Ni ]]The reason for the FCC phase of (a). With the addition of TiN, the lattice distortion of TiN becomes more and more serious, and the increase of TiN distribution at the interface of FCC and BCC is also the main reason for breaking and reducing the breaking strain. The FCC phase has good soft plasticity, and the hardness and strength of the FCC phase are obviously improved under the condition of sacrificing a certain plasticity due to the addition of TiN and the presence of the BCC phase. It is obvious that the molding toughness and the toughness can be achieved under the condition of improving the overall hardness by controlling the addition amount of TiN.
FIG. 8 shows Al0.5Cr0.9FeNi2.5TiNxThe electron microscope photo of the wear morphology of the alloy, wherein (a, c, e, g, i, k) is the wear morphology under 200 times, it can be easily seen that the wear width gradually decreases with the increase of the TiN content, which indicates that the wear resistance gradually increases. The figure (b, d, f, h, j, l) is 1k times of the appearance corresponding to the previous figure, when TiN is added, the furrow is deepest, the falling object is flaked and falls off, the falling phenomenon is most serious, and the abrasion is carried outThe damage mechanism is adhesive wear and abrasive wear. With the increase of TiN content, the furrow becomes shallow gradually, the falling particles become small, when x is more than or equal to 0.6, basically no falling object exists, and the abrasion mechanism at the moment is abrasive abrasion.
Generally, the degree of wear is related to the resistance of the contact surface during friction, and the greater the resistance, the greater the degree of wear. The reason for this phenomenon is mainly that the magnitude of the shearing force applied to the surface of the alloy sample is mainly determined by the frictional resistance, and the larger the frictional resistance is, the larger the shearing force applied to the particles on the surface of the alloy sample is, and therefore, the particles are more likely to fall off in a frictional environment with large resistance.
The reasons for this are mainly that the addition increases, which makes the FCC lattice distortion become more and more severe (when x is 0.8, the lattice distortion constant is the largest), the structure between the crystal grains is more compact, the dislocation is not easy to occur, and the macro is reflected by the increase of hardness and wear resistance. The TiN is a hard phase which is macroscopically and uniformly distributed, and is one of the reasons for reducing the falling objects. The two work together to make the friction coefficient lowest and the falling object relatively less when x is 0.8.
As can be seen from fig. 9, the change in the friction coefficient is closely related to the content of TiN added, and the friction coefficient is minimized to about 0.45 when x is 0.8. It can be directly seen that the increase of TiN element makes the friction coefficient of the alloy become smaller, while the friction coefficient gradually increases with time and then tends to be flat. The addition of TiN element increases the wear resistance of the alloy and tends to be saturated to a certain extent.
And Al0.5Cr0.9FeNi2.5TiNxThe friction coefficient curve of the multi-principal element alloy tends to be stable in about 2 minutes, and changes from severe abrasion to stable abrasion, because the small ball is in point contact or incomplete surface contact with the sample due to mechanical processing problems at first, the friction coefficient in the period of time does not reach a steady state, and the friction coefficient is influenced by the condition of a friction contact surface to a great extent, so that the friction coefficient curve is inaccurate. In the stage of stable abrasion, the friction coefficient reaches a stable state and does not fluctuate severely any more, and the friction coefficient in the stage is accurate.
Therefore, it is concluded that the addition of TiN reaches an optimal state around x 0.8, which promotes the generation of BCC phase, and also limits the nucleation of BCC to some extent, and many nanoparticles appear, so that the hardness, strength, plasticity and wear resistance of the alloy reach an optimal ratio at this moment, and the comprehensive mechanical properties of the alloy are improved.
The key point of the invention is to research novel Al0.5Cr0.9FeNi2.5TiNxThe influence of TiN content in the multi-principal element alloy on the structure performance. The content of TiN is increased, more body-centered cubic structures can be formed, and various mechanical properties can be improved due to the transformation of the structure and the phase. Al (Al)0.5Cr0.9FeNi2.5TiNxThe multi-principal component alloy structure is composed of two FCC phases, a BCC phase and TiN inclusions, when the alloy structure does not contain TiN, namely x is 0.0, the alloy structure only contains the FCC phase, the BCC phase is gradually precipitated along with the increase of the TiN content, the lattice distortion constant is increased, and the maximum value is reached when x is 0.8. The solid solution strengthening effect and the second phase strengthening effect of the alloy structure are gradually strengthened along with the increase of the content of TiN, the microhardness is increased, and the maximum value is reached when x is 1.0 and is 657.74 Hv. The plastic fracture strength of the alloy increases with the increase of the content of TiN, but the strain at fracture decreases with the increase of the content of TiN, and the two are optimal when x is 0.8, and the fracture strength is 2006 MPa. Al (Al)0.5Cr0.9FeNi2.5TiNxThe friction coefficient of the multi-principal element alloy is reduced along with the increase of the content of TiN, and on the contrary, the wear resistance of the multi-principal element alloy is gradually improved along with the increase of the content of TiN, and reaches the maximum when x is equal to 0.8. It can be seen that the overall performance is optimized at x of 0.8.
The above description is only a preferred embodiment of the present invention, and is not intended to limit the present invention in any way, and all simple modifications and equivalent variations of the above embodiment according to the present invention are within the scope of the present invention.
Claims (5)
1. A multi-principal-element alloy with high toughness and plasticityThe multi-principal element alloy has the following structure: in terms of mole ratio, Al0.5Cr0.9FeNi2.5(TiN)xX is 0.2, 0.4, 0.6, 0.8, 1.0; the preparation method of the multi-principal-element alloy comprises the following steps:
1) accurately weighing smelting raw materials by using an electronic balance, and adopting pure metals of Al, Cr, Fe and Ni and purity>99% of TiN particles, respectively in terms of mole fraction Al0.5Cr0.9FeNi2.5(TiN)xPreparing x is 0.2, 0.4, 0.6, 0.8 and 1.0;
2) vacuum arc melting: vacuumizing an electric arc furnace, then carrying out electric arc melting under the atmosphere of high-purity argon at the current of 150A-300A to prepare Al0.5Cr0.9FeNi2.5(TiN)x0.2, 0.4, 0.6, 0.8 and 1.0 alloy ingot;
the Al is0.5Cr0.9FeNi2.5(TiN)xThe alloy ingot with x being 0.2, 0.4, 0.6, 0.8, 1.0 has a maximum breaking strength of 2006MP a.
2. The high strength ductile multi-element alloy according to claim 1, wherein said multi-element alloy has the following structure: in terms of mole ratio, Al0.5Cr0.9FeNi2.5(TiN)0.8The high Ni/Al ratio of the multi-element alloy in combination with the additive elements promotes the formation of the BCC phase.
3. The high toughness multi-element alloy as claimed in claim 1, wherein the degree of vacuum applied in step 2) is (4.5-4.8) × 10-3Pa。
4. The high strength ductile multi-element alloy according to claim 1, wherein the purity of the high purity argon gas in step 2) is more than 99.999%, and the high purity argon gas is filled to a vacuum degree of-0.05 MPa.
5. A high strength ductile multi-element alloy according to claim 1 wherein said ingot in step 2) is melted, inverted and remelted at least 5 times to improve chemical homogeneity.
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