CN116904813A - Novel high-strength and high-toughness corrosion-resistant aluminum alloy material gene design method and laser additive manufacturing preparation method - Google Patents
Novel high-strength and high-toughness corrosion-resistant aluminum alloy material gene design method and laser additive manufacturing preparation method Download PDFInfo
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Abstract
The invention discloses a material gene design method and a laser additive manufacturing preparation method of a novel high-strength and high-toughness corrosion-resistant aluminum alloy. The invention successfully constructs a database of the components of the aluminum alloy with the toughness and the corrosion resistance in the material gene design, and designs the novel aluminum alloy powder of AlMgZnCuErZr with high toughness and good corrosion resistance. At 639-1157J/cm 3 Optimizing laser cladding process parameters in laser energy density rangeThe prepared AlMgZnCuErZr aluminum alloy sample not only has good laser printability, but also has a matching relation between high toughness and good corrosion resistance, the compressive strength is in the range of 580-663 MPa, the deformation is 12.5-15%, and the toughness is 36-39 MPa.m 1/2 And the corrosion potential variation range is-0.78 to-0.71V.
Description
Technical Field
The invention belongs to the technical field of high-performance aluminum alloy manufacturing by laser additive, and particularly relates to a material gene design method and a laser additive manufacturing preparation method of a novel high-strength and high-toughness corrosion-resistant AlMgZnCuErZr aluminum alloy.
Background
The laser additive manufacturing technology can rapidly prepare parts with complex geometric shapes, reduce the connection of multiple components, ensure high quality and achieve the effect of reducing the weight of the structure, so the laser additive manufacturing technology is widely applied to manufacturing and remanufacturing of relevant core parts in the fields of aerospace, traffic, machinery and the like in recent years. With the rapid development of new materials, new processes and new equipment, the laser additive manufacturing technology has rapidly developed in the directions of high-strength toughening of materials, light structure, intelligent preparation process, high performance and low cost of formed products and the like. Especially, for the laser additive manufacturing of key parts with large complex structures in the application field, such as manufacturing parts of high-speed railway brake discs, rocket fuel nozzles, aircraft thin-wall structure air inlets and the like, the requirements on novel aluminum alloy materials with light weight, high heat conductivity, high precision, high bearing capacity and structures, advanced forming process technology, high-strength and toughness tissue performance regulation technology and the like are higher and higher. Therefore, research on a novel aluminum alloy material for laser additive manufacturing, which is light in weight, high in strength and toughness and corrosion resistant, and an advanced forming technology thereof has become one of the new important research subjects.
At present, a plurality of important progress has been made in research on high toughness and corrosion resistance of aluminum alloy manufactured by laser additive, mainly by adjusting the type of aluminum alloy phase,The shape and the number are used for regulating and controlling the comprehensive performance. If the AlSi10Mg alloy with wider application is used, the solidification range is smaller (about 50 ℃), the AlSi10Mg alloy is not easy to crack and deform during printing, and the formed netlike eutectic Si and Mg are 2 Si produces precipitation strengthening to have a tensile strength of about 480MPa and a yield strength of about 260MPa, but has insufficient toughness. The rare element-modified AlMgScZr alloy has excellent laser printability (solidification range of about 55 ℃ C.) due to the diversified components. Comparing AlMgScZr with AlSi10Mg, the strength and toughness of the former were found to be superior to the latter. This is because the former forms Al 3 (Sc 1-x ,Zr x ) The precipitated phase is pinned at the grain boundary to effectively prevent dislocation sliding, so that the dislocation has good processing hardenability, welding property and toughness. However, sc is too expensive, so that the content of the reinforcing phase is limited, and the toughness is difficult to further improve. So the laser additive manufacturing of the high-strength aluminum alloy with multiple components becomes a new breakthrough point.
However, the current research shows that the laser additive manufacturing of high-strength aluminum alloy such as AlCuMg, alZnMgCu has a larger solidification zone (higher than 100 ℃), coarse columnar crystals or hot cracks and other defects can be generated in the rapid melting and solidification process of the additive manufacturing, and the toughness matching is difficult to meet the application requirements. Even the high-strength aluminum alloy prepared by the traditional casting, cold pressing, hot rolling, hot pressing and other processes also has the problem of toughness regulation and control, for example, alCuMg has good toughness, low strength, alZnMgCu has good strength, insufficient toughness and poor deformability, and is difficult to break through the yield strength higher than 400MPa and the toughness reaching 35 MPa.m 1/2 Is matched with the strength and toughness of the steel plate. In addition, the toughness and corrosion resistance of the aluminum alloy manufactured by laser additive are difficult to be compatible, such as Al for improving the strength of the aluminum alloy manufactured by laser additive 3 Mg 2 、Al 2 Cu、Al 2 CuMg、MgZn 2 And a micro battery is formed between the precipitated phase and the alloy matrix, so that electrochemical corrosion of the alloy is promoted, and the corrosion resistance of the alloy is reduced. Based on the above research summary, the aluminum alloy materials meeting the printability of laser additive manufacturing at the present stage are less in variety; the toughness matching research of the steel has a bottleneck; design and preparation research on laser additive manufacturing aluminum alloy with toughness and corrosion resistance are difficult to break through. Because ofThe innovative research can meet the unbalanced metallurgical characteristics of laser additive manufacturing, and has the novel aluminum alloy powder with high toughness, corrosion resistance and low cost, so that a foundation can be laid for the preparation of high-performance parts such as brake discs.
Disclosure of Invention
In view of the design difficulty of the easily-cracked components of the unbalanced solidification aluminum alloy and the requirements of the bearing aluminum alloy structural part on light weight, high strength and high toughness and corrosion resistance of the material performance in the prior art, the invention aims to provide a genetic design and preparation method for manufacturing a novel high strength and toughness corrosion-resistant AlMgZnCuErZr aluminum alloy by laser material addition. Specifically comprises adopting a material gene design method to select enhanced T-Mg according to the design thought of toughness corrosion resistance, key gene phase and multiple components 32 (AlZnCu) 49 And Mg (magnesium) 2 Si, toughened alpha-Al, al 3 Zr and Al 3 (Er, zr) and corrosion resistant A1 6 Mn is used as a key gene phase of a novel aluminum alloy material, and a novel high-strength and high-toughness corrosion-resistant AlMgZnCuErZr aluminum alloy powder component for laser additive manufacturing is constructed by optimizing aluminum alloy components by utilizing a computer algorithm and a thermodynamic theory through establishing a theoretical prediction model. The method optimizes the laser cladding process parameters to prepare an aluminum alloy sample with three gene phases and good laser printability, toughness and corrosion resistance, clarifies the influence mechanism of reinforcing genes, toughening genes and corrosion resistance genes on the performance of the laser cladding aluminum alloy, and provides an integrated advanced technology of material gene design, laser process preparation and tissue performance regulation. The performance of the novel aluminum alloy is regulated and controlled by regulating and controlling the gene phase proportion of the laser energy density, so that the novel aluminum alloy breaks through the compression strength of more than 550MPa and has the toughness of more than 35 MPa.m 1/2 And technical indexes that the corrosion potential is higher than-0.8V.
In order to achieve the above purpose, the present invention adopts the following technical scheme:
the invention provides a material gene design method of high-strength and high-toughness corrosion-resistant aluminum alloy powder components for laser additive manufacturing, which is characterized by comprising the following steps of: the method comprises the following steps:
(1) Defining a key gene phase, said key gene phaseComprises a key enhancement gene phase, a key toughening gene phase and a key corrosion resistant gene phase, wherein the key enhancement gene phase is T-Mg 32 (AlZnCu) 49 、Al 3 Zr and Al 3 (Er, zr); the key toughening gene phase is alpha-Al, and the key corrosion resistant gene phase is Al 6 Mn；
(2) According to the defined key gene phase, determining a first candidate component serving as an aluminum alloy component, wherein the first candidate component consists of the following metal elements in percentage by mass: mg:0-14.1%, zn:0-9%, cu:0-6.8%, mn:0-2%, si 0-6.5%, er:0-0.66%, zr:0-0.44;
(3) Setting variation according to the content of each metal element, and establishing a first database taking aluminum alloy components composed of the metal elements with different contents as basic unit data;
(4) Screening the data of the first database according to a screening standard to obtain a second database;
(5) Calculating solid solution strengthening factors, precipitation strengthening factors and solidification intervals of different aluminum alloy components in the second database according to solute concentration, volume fractions of precipitated phases and the solidification intervals as parameters, and establishing a three-dimensional model taking the solid solution strengthening factors, the precipitation strengthening factors and the solidification intervals as coordinate axes to obtain aluminum alloy powder components;
wherein, in step (4), the screening criteria are: cu/Mg <0.5, zn/Mg <1, si=0.4-0.6%, er=0.5-0.7% and zr=0.3-0.5%.
In the step (5), the solute concentration is the concentration of Mg, zn and Cu, and the volume fraction of the precipitated phase is the alpha-Al, T-Mg 32 (AlZnCu) 49 、Al 6 Mn、Al 3 Zr and Al 3 (Er, zr), wherein the solidification range is 0-200deg.C, the solid solution strengthening factor is the sum of the solid solution strengthening effects of Mg, zn and Cu, and the precipitation strengthening factor is the alpha-Al, T-Mg 32 (AlZnCu) 49 、Al 6 Mn、Al 3 Zr and Al 3 (Er, zr) in the total of the precipitation strengthening effects.
In the above screening criteria, asConditions for generating T key gene phase, and Zn/Mg is set<1 and Cu/Mg<0.5; as a embrittlement-reducing phase Mg 2 Conditions for reducing the thermal cracking sensitivity of Mg while reducing the amount of Si produced, si=0.4 to 0.6% are set; considering the cost of the new alloy and referring to the commercial al4.6mg0.66sc0.42zr alloy, er=0.5-0.7% and zr=0.3-0.5% are set.
In the above technical scheme, the concentrations of Mg, zn and Cu are 0-20at%, 0-3.3at% and 0-0.78at%, respectively, and the alpha-Al and T-Mg are as follows 32 (AlZnCu) 49 、Al 6 Mn、Al 3 Zr and Al 3 The volume fraction of (Er, zr) is 50-85 wt%, 0-40 wt%, 0-10 wt%, 0-1 wt% and 0-1 wt%, the value range of the solid solution strengthening factor is 0-110MPa, and the value range of the precipitation strengthening factor is 0-200MPa.
In a second aspect of the present invention, there is provided a high-strength and high-toughness corrosion-resistant aluminum alloy powder for laser additive manufacturing, the composition of which is obtained according to the above-described material gene design method.
In the technical scheme, the high-strength and high-toughness corrosion-resistant aluminum alloy powder for laser additive manufacturing comprises the following metal elements in percentage by mass: al:66-68%, mg:13-15%, zn:8-10%, cu:5-7%, mn:1.5-2.5%, si:0.4-0.6%, er:0.5-0.7%, zr:0.3-0.5%.
In the technical scheme, the preparation method of the high-strength and high-toughness corrosion-resistant aluminum alloy powder for laser additive manufacturing comprises the following steps of: according to the mass percentage, taking pure simple substance powder of each metal element, and mechanically mixing for 5-10 hours under the conditions that the ball-material ratio is 1:2 and the rotating speed is 350r/min to obtain aluminum alloy powder, wherein the average grain diameter of the aluminum alloy powder is 40-50 mu m.
The invention provides a laser cladding preparation method of a high-strength and high-toughness corrosion-resistant AlMgZnCuErZr aluminum alloy material, wherein the AlMgZnCuErZr aluminum alloy material is prepared by molding the high-strength and high-toughness corrosion-resistant aluminum alloy powder for laser additive manufacturing through a laser cladding process.
In the technical proposal, the high-strength and high-toughness corrosion-resistant aluminum for laser additive manufacturing is used on the substrateThe alloy powder is a powder paving raw material, and the high-strength high-toughness corrosion-resistant AlMgZnCuErZr aluminum alloy material is prepared under the surface scanning path by a laser cladding process, wherein the parameters of the laser cladding process are as follows: the substrate is preheated to 200 ℃, and the energy density of the laser is 639-1157J/cm 3 。
In the technical scheme, the structure of the AlMgZnCuErZr aluminum alloy material prepared by the laser cladding process comprises the following components in percentage by volume: 54-75% of alpha-Al gene phase and 24-35% of T-Mg 32 (AlZnCu) 49 Gene phase, 5.4-8.3% Al 6 Mn gene phase, 0.8-1.3% Mg 2 Si gene phase, less than 5% Al 3 Zr and Al 3 (Er, zr) gene phase.
In the technical proposal, the density of the AlMgZnCuErZr aluminum alloy material prepared by the laser cladding process is 99.52 percent to 99.85 percent, the hardness range is 178 HV to 187HV, and the compressive strength (sigma) bc ) Is 580-663 MPa, and the yield strength (sigma) ys ) Is 415-420 MPa, deformation (epsilon) c ) 12.5-15%, toughness (K) IC ) Is 36-39 MPa.m 1/2 The corrosion potential is-0.78 to-0.71V, and the corrosion current density is 1.14X10 -6 ～1.35×10 -6 A/cm 2 。
Compared with the prior art, the invention has the following advantages:
1. the invention successfully establishes a material gene design method of novel AlMgZnCuErZr alloy powder suitable for laser cladding of high-performance parts. The method can rapidly optimize target components meeting the unbalanced metallurgical characteristics of laser and having toughness and corrosion resistance according to target performances by defining genes, establishing screening standards, calculating, experiment and database searching, and rapidly complete the design of high-performance aluminum alloy components.
2. The preparation of the high-density novel AlMgZnCuErZr aluminum alloy sample is realized by optimizing the laser energy density. The novel laser cladding aluminum alloy has good matching relation of laser printability, high strength and toughness and corrosion resistance. Solves the difficult problem of easy cracking of the novel high-strength corrosion-resistant aluminum alloy by laser cladding.
3. The product of the compressive strength and the deformation of the laser cladding novel alloy sample is improved by 13.44 percent compared with the high-strength AlZnMgCu alloy prepared by the traditional method.
4. The integrated advanced technology of material gene design, laser process preparation and tissue performance regulation is obtained, and theoretical and technical references are provided for laser additive manufacturing, high-strength toughness and corrosion resistance aluminum alloy component design and high-performance part preparation.
Drawings
FIG. 1 is a screen shot of the novel aluminum alloy element range, database composition screening and simulation process used in example 1.
FIG. 2 is the three-influence factor calculation result of the gene design model in example 1: (a) Calculating partial screenshot of solid solution strengthening factors, precipitation strengthening factors and a calculation result of a solidification interval for the JMat pro software, and (b) summarizing a corresponding generated three-dimensional simulation calculation result.
FIG. 3 is a metallographic photograph of laser cladding samples prepared in examples 2-4 at different laser energy densities.
FIG. 4 is a graph of laser cladding sample density at different laser energy densities prepared in examples 2-4.
Fig. 5 is a schematic drawing of a sample of laser clad aluminum alloy prepared in example 2.
FIG. 6 is a scanned photograph of the laser cladding Al14Mg9Zn6Cu2Mn0.5Si0.4Zr0.6Er aluminum alloy prepared in example 2 in the back scattering mode: (a) Is microstructure morphology, (b) - (i) is (a) drawing scanning energy spectrum result, (j) is amplified phase and energy spectrum.
Fig. 7 is an XRD pattern of the laser clad AlMgZnCuErZr aluminum alloy prepared in example 2.
FIG. 8 is an EBSD of the laser clad AlMgZnCuErZr aluminum alloy prepared in example 2.
Fig. 9 is a transmission photograph of the laser cladding AlMgZnCuErZr aluminum alloy prepared in example 2.
FIG. 10 is a graph of the performance of the laser clad AlMgZnCuErZr aluminum alloys prepared in examples 2-4 versus the aluminum alloys prepared in the conventional manner, (a) compressive strength versus deflection, and (b) yield strength versus toughness.
Detailed Description
The following non-limiting examples will enable those of ordinary skill in the art to more fully understand the invention and are not intended to limit the invention in any way. In the examples which follow, the experimental procedure used is conventional, and the reagents and materials, unless otherwise indicated, are commercially available.
It should be noted that, without conflict, the embodiments of the present invention and features of the embodiments may be combined with each other.
Example 1
The material gene design method of the high-strength and high-toughness corrosion-resistant aluminum alloy powder component for laser additive manufacturing is implemented according to the following steps:
1. defining key gene phases: according to the requirement of the laser cladding light-weight key parts on the novel high-toughness and corrosion-resistant aluminum alloy material, three key gene phases are defined, namely a key reinforcing gene phase, a key toughening gene phase and a key corrosion-resistant gene phase, wherein the key reinforcing gene phase is T-Mg 32 (AlZnCu) 49 、Al 3 Zr and Al 3 (Er, zr); the key toughening gene phase is alpha-Al, and the key corrosion resistant gene phase is Al 6 Mn。
2. Determining each metal element and the content thereof in the alloy according to the key gene phase defined in the step 1, and obtaining a first candidate component of aluminum alloy powder, wherein the first candidate component comprises the following metal elements in percentage by mass: mg:0-14.1%, zn:0-9%, cu:0-6.8%, mn:0-2%, si 0-6.5%, er:0-0.66%, zr:0-0.44%. The determination of the content range of each metal element in the alloy is performed based on the determination of the content range of each metal element shown in table 1.
TABLE 1 screening conditions for the content ranges of alloying elements and reasons for this determination
3. According to the content range of each metal element, the component variation of each metal element (such as the element range in fig. 1) is determined, a database is established, and 3176712 aluminum alloy components (a first database) are established in total, as shown in the partial screenshot of the total composition table in the database in fig. 1.
4. And establishing a theoretical prediction model and screening standards. And determining the optimal component by taking the solid solution strengthening, the second phase strengthening and the solidification interval as a three-dimensional model. Screening criteria were established as shown in table 1: cu/Mg<0.5、Zn/Mg<1. Si=0.5%, er=0.5-0.7% and zr=0.3-0.5%. After preliminary screening, the types of aluminum alloy components were reduced from 3176712 to 49844 (second database), as shown in the partial results of the composition table after screening in the database of fig. 1. And calculating solid solution strengthening factors, precipitation strengthening factors and solidification intervals of different aluminum alloy components in the second database by taking solute concentrations, precipitated phase volume fractions and solidification intervals of the different aluminum alloy components simulated by JMatPro software as parameters, and establishing a three-dimensional model taking the three factors as coordinate axes to obtain optimal components, wherein the screenshot of the high-throughput calculation process is shown in fig. 1. Wherein, the solute concentration refers to the concentration of Mg, zn and Cu as main solid solution atoms, and the concentration ranges are 0-20at%, 0-3.3at% and 0-0.78at%, respectively; the volume fraction of the precipitated phase refers to the key gene phase alpha-Al, T-Mg 32 (AlZnCu) 49 、Al 6 Mn、Al 3 Zr and Al 3 Volume fraction of (Er, zr) in the range of 50-85wt.%, 0-40wt.%, 0-10wt.%, 0-1wt.% and 0-1wt.%, respectively; the solidification zone is a temperature zone in which all aluminum alloy components are converted from a liquid state to a solid state, and the solidification zone is in the range of 0-200 ℃. The solid solution strengthening factor is the sum of the solid solution strengthening effects of three solid solution atoms of Mg, zn and Cu and is 0-110MPa, and the precipitation strengthening factor is alpha-Al and T-Mg 32 (AlZnCu) 49 、Al 6 Mn、Al 3 Zr and Al 3 The sum of precipitation strengthening effects of precipitation phases of (Er, zr) is 0-200MPa, the aluminum alloy powder components meeting the requirements are aluminum alloy powder components with high solid solution strengthening factors matched with the precipitation strengthening factors and small solidification intervals, the sum of the high solid solution strengthening factors matched with the precipitation strengthening factors is more than 250MPa, and the small solidification intervals are less than 60 ℃.
5. High throughput computing optimaThe components are as follows. FIG. 2 (a) is a partial screenshot of the calculation results of three influencing factors (solute concentrations of different components, volume fractions of precipitated phases and solidification intervals) of a theoretical model, in which no corrosive phase (. Beta. -Al) is generated 3 Mg 2 Phase S "-Al 2 Solid solution strengthening factor (IF sigma) of CuMg phase) component sol ) Precipitation strengthening factor (IF sigma) pre ) And the result of the solidification zone is extracted and plotted into a three-dimensional simulation calculation result summary diagram shown in fig. 2 (b). According to the three-dimensional image, the optimal alloy comprises the following components in percentage by mass: al:66-68%, mg:13-15%, zn:8-10%, cu:5-7%, mn:1.5-2.5%, si:0.4-0.6%, er:0.5-0.7%, zr:0.3-0.5%.
Example 2
Preparing a novel aluminum alloy sample by adopting a laser cladding process, specifically comprising the following steps:
(1) Composition of AlMgZnCuErZr aluminum alloy powder: the chemical components of the material in percentage by mass are: al:67.5%, mg:14%, zn:9%, cu:6%, mn:2%, si:0.5%, er:0.6%, zr:0.4%.
(2) Preparation of AlMgZnCuErZr aluminum alloy powder: pure elemental metal powders of the respective metal elements were prepared, and the average particle diameter was 40 μm to 50. Mu.m. According to the composition ratio of the aluminum alloy powder, each simple substance metal powder is put into a ball mill, and the weight ratio of the ball materials is 1 when the rotating speed is 350 r/min: 2, mechanically mixing for 7.5 hours under the parameter of 2, so that different elements are uniformly distributed, and the AlMgZnCuErZr aluminum alloy powder with the average particle size of 40-50 μm is obtained.
(3) Preparing a novel aluminum alloy sample by adopting a laser cladding process: the equipment used was FL-Dlight02-3000W semiconductor laser (spot size 4X 4 mm) 2 ) The adopted substrate is an Al5083 aluminum plate, the aluminum plate is subjected to polishing treatment in advance, the surface of the aluminum plate is leveled, and the substrate is preheated to 200 ℃. The AlMgZnCuErZr aluminum alloy powder prepared in the step (2) adopts a FL-Dlight02-3000W semiconductor laser (the spot size is 4 multiplied by 4 mm) 2 ) Powder spreading printing was performed, the shape and printing path of the print body were set with self-contained programming software, and AlMgZnCuErZr aluminum alloy powder was laser-clad on the substrate, to prepare a laser-clad AlMgZnCuErZr aluminum alloy sample (hereinafterSimply referred to as laser clad aluminum alloy samples). Laser cladding process parameters: the laser energy density is 1157J/mm 3 (2500W, 3 mm/s), the powder layer thickness (t) is 0.3mm, the scanning interval (d) is 2.4mm (lap ratio is 40%), the scanning path is a face scan, and the preparation of the laser cladding aluminum alloy sample is completed in an argon protection environment.
Performance test of laser cladding aluminum alloy sample:
and (3) verifying printability of a laser cladding aluminum alloy sample: FIG. 3 (c) shows that the laser energy density of the laser cladding aluminum alloy sample is 1157J/mm 3 The metallographic morphology at (2500W, 3 mm/s) showed a denser structure, no crack, only a small number of holes, and a statistical density of about 99.85% by area method (FIG. 4).
Verification of gene phase generation: in order to further analyze the microstructure of the laser cladding aluminum alloy sample, the laser cladding aluminum alloy sample is taken parallel to the YZ surface as shown in fig. 5, and the microstructure type and the content of the sample are analyzed under an OLMPUS-GX71 metallographic microscope and a JSM-7001F field emission scanning electron microscope provided with an energy spectrum (EDS) probe, and the results are shown in fig. 6, and indicate that 59vol.% alpha-Al and 33vol.% T-Mg are generated in situ for the laser cladding aluminum alloy sample 32 (AlZnCu) 49 、7vol.％Al 6 Mn、1vol.％Mg 2 Si and a small amount of Al 3 Zr、Al 3 The (Er, zr) critical gene phase and its energy spectrum information are counted in table 2, XRD-7000X-ray diffractometer (XRD) is selected to perform phase analysis on the polished sample before and after printing under the continuous scanning condition of 5 °/min, the result is shown in fig. 7, the XRD analysis result corresponds to the microstructure type shown in fig. 6, the Electron Back Scattering (EBSD) sample prepared by argon ion polishing is used to analyze the grain size, the result is shown in fig. 8, the crystal grain of the novel alloy sample is equiaxed fine crystal, and the statistical average grain size is 2.43 μm. Further observation of the nano-scale precipitated phase under JEM-2100F transmission electron microscope, the results are shown in FIG. 9, which shows some smaller Al 3 Zr and Al 3 The (Er, zr) phase is distributed within the T phase and the a-Al phase, and others are distributed at the grain boundaries, promoting the formation of equiaxed fine crystals (fig. 8).
From the scan of FIG. 6, the results of Table 2, the XRD pattern of FIG. 7, and the transmission of FIG. 9, it was determined that the laser cladding sample was originally produced an alpha-Al key toughening gene phase, T-Mg 32 (AlZnCu) 49 And a small amount of Al 3 Zr、Al 3 (Er, zr) Critical enhancement Gene phase and Al 6 Mn is a key corrosion-resistant gene phase, and the feasibility of generating a three-gene phase in situ by laser cladding of the novel aluminum alloy is verified.
TABLE 2 EDS quantitative analysis of positions marked Point 1-Point 4 in FIG. 6 (a), phase content of Key Gene phase species and area method statistics
Verifying the toughness of the laser cladding aluminum alloy sample: the uniaxial compression test is carried out on an AG-XPLUS100KN electronic universal tester, the sampling direction of a sample is shown in figure 4, and the size of the sample is phi 3 x 4mm 3 Is a cylinder with a compressive strain rate of 5 x 10 -3 s -1 Each group was tested for 3 parallel samples. The hardness of the sample in the stacking direction is tested by adopting an MHV 2000 digital Vickers microhardness tester, the loading load is 50g, and the dwell time is 10 s. The room temperature fracture toughness was measured by measuring the average propagation distance of microcracks by dotting a laser clad aluminum alloy sample under a load of 50kg (490N) and a pressure maintaining condition of 60s using a vickers hardness tester (VH-500 AC). The results are shown in Table 3.
TABLE 3 laser energy Density of 1157J/mm 3 Summary of average hardness, compressibility, toughness, and corrosion properties of laser clad aluminum alloy samples
Table 3 shows that at an energy density of 1157J/mm 3 When the laser isThe average hardness of the cladding aluminum alloy sample is 178+/-3 HV, and the compressive strength (sigma) bc ) 663+ -13 MPa, yield strength (σ) ys ) 419+ -18 MPa, deformation (. Epsilon.) c ) 15.+ -. 1%. Obtaining fracture toughness (K) by measuring microcrack propagation distance method at room temperature of small sample IC ) About 39.+ -. 3 MPa.m 1/2 。
The properties of the laser cladding AlMgZnCuErZr aluminum alloy and the high strength aluminum alloy prepared by the conventional preparation methods such as cold pressing, hot rolling, hot pressing, casting, hydraulic pressure and the like are shown in FIGS. 8 (a) and (b). The comparison shows that the product of the compression strength and the deformation of the laser cladding sample is 13.44% higher than that of the AlZnMgCu alloy. Its high strength is attributed to solid solution strengthening of alpha-Al and T-Mg 32 (AlZnCu) 49 、Al 6 Mn、Mg 2 Dispersion strengthening and Al formed by Si reinforcing gene phase 3 Zr、Al 3 Ordered strengthening and fine grain strengthening of (Er, zr) enhanced gene phase formation. While the high toughness is attributed to dense texture reducing crack sources, al 6 Mn micron-sized precipitated phase deflects and toughens crack propagation paths, al 3 Zr、Al 3 Equiaxed fine grain toughening formed by (Er, zr) toughening gene phase, and crack bridge toughening generated by a plurality of unit structures formed by net-shaped T phase and alpha-Al phase of a screen structure.
And verifying corrosion resistance of the laser cladding aluminum alloy sample: the sample direction of the electrochemical test sample is parallel to the YZ direction in fig. 4, and the electrochemical polarization curve of the sample is determined using an electrochemical workstation model CS 350. The working electrode is a novel alloy sample for laser cladding, the auxiliary electrode is a platinum electrode, the reference electrode is a glycerol electrode, and the test solution is 3.5wt.% NaCl solution. The electrochemical test parameters were set to an initial potential of-0.5V versus open circuit potential, a termination potential of 0.5V versus open circuit potential, and a scan rate of 0.5mV/s. The corrosion potential and current density of the laser cladding aluminum alloy samples are summarized in Table 3, wherein the average corrosion potential is-0.71.+ -. 0.03V, and the corrosion current density is (1.14.+ -. 0.02). Times.10 -6 A/cm 2 Comparing with the electrokinetic polarization results of other aluminum alloy samples prepared by laser cladding and as-cast, as shown in Table 4, the AlMgZnCuErZr aluminum alloy samples were laser cladThe corrosion voltage is relatively high, and the corrosion current density is small, so that the corrosion resistance is good.
TABLE 4 comparison of potential polarization results of laser cladding AlMgZnCuErZr aluminum alloy and other constituent aluminum alloy samples
Example 3
The preparation method of the novel aluminum alloy sample by adopting the laser cladding process is basically the same as the steps (1) to (3) of the embodiment 2, except that a higher laser energy density of 3472J/mm is adopted 3 Printing is performed.
The prepared laser cladding aluminum alloy sample is subjected to performance test, including printability verification, tissue gene phase verification, toughness verification, corrosion resistance verification and the like, and the verification method is the same as that of the example 2, and the verification result is as follows:
as shown in FIG. 3 (d), the AlMgZnCuErZr sample was clad with laser light at a laser energy density of 3472J/mm 3 When the metallographic morphology of the laser cladding sample is found, the laser cladding sample has no crack generation under higher energy density, the number of holes is slightly increased, and the statistical density by an area method is 99.56%. Characterization of the tissue gene phase showed that at 3472J/mm 3 The alloy sample structure prepared at laser energy density consists of 54vol.% of alpha-Al, 35vol.% of T-Mg 32 (AlZnCu) 49 、8.3vol.％Al 6 Mn、1.3vol.％Mg 2 Si and a small amount of Al 3 Zr、Al 3 The (Er, zr) key gene phase. The results of the examination of toughness and corrosion resistance are shown in Table 5, and the average hardness is 153HV, and the average compressive strength (σ bc ) 640MPa, yield strength (sigma ys ) 426MPa, deformation (. Epsilon.) c ) 13.8% and toughness of 38MPa.m 1/2 Average self-corrosionThe potential was-0.74V, and the corrosion current density was 1.26X10 -6 A/cm 2 . 1157J/mm as used in example 2 3 The hardness of the prepared laser cladding sample is reduced compared with that of the prepared laser cladding sample, but the compressive strength, the deformation and the toughness are reduced due to the increase of the number of holes. Comparing the high-strength AlZnMgCu alloy (figure 8) prepared in the conventional way, the product of the compression strength and the deformation of the laser cladding sample is found to be close to that of the AlZnMgCu alloy which is difficult to carry out laser printing. The increase of holes increases the corrosion speed, reduces the corrosion potential and improves the corrosion current density. But still more corrosion resistant than the corrosion performance of the other component alloys in table 4.
TABLE 5 laser energy Density of 639J/mm 3 Summary of average hardness, compressive properties, and toughness of time-laser clad aluminum alloy samples
Example 4
The novel aluminum alloy samples were prepared by a laser cladding process, which was prepared in substantially the same manner as in steps (1) to (3) of example 2, except that a lower laser energy density of 694J/mm was used 3 Printing is performed.
The prepared laser cladding aluminum alloy sample is subjected to performance test, including printability verification, tissue gene phase verification, toughness verification, corrosion resistance verification and the like, and the verification method is the same as that of the example 2, and the verification result is as follows:
as shown in FIG. 3 (b), the laser energy density of AlMgZnCuErZr sample obtained by laser cladding was 694J/mm 3 When the metallographic morphology of the laser cladding sample is used, the sample laser cladding sample still has no crack generation under the condition of lower energy density, the number of holes is slightly increased, and the statistical density is 96.8%. Characterization of the tissue Gene phase revealed that the gene phase was found to be at 694J/mm 3 The alloy sample structure prepared at laser energy density consists of 75vol.% alpha-Al, 19vol.% T-Mg 32 (AlZnCu) 49 、5.4vol.％Al 6 Mn、0.8vol.％Mg 2 Si and a small amount of Al 3 Zr、Al 3 The (Er, zr) key gene phase. The results of the examination of toughness and corrosion resistance are shown in Table 6, and the average hardness was 187HV, and the average compressive strength (σ bc ) At 580MPa, yield strength (σ) ys ) 415MPa, deformation (. Epsilon.) c ) 12.5%, toughness 34 MPa.m 1/2 The average self-corrosion potential was-0.78V, and the corrosion current density was 1.35X 10 -6 A/cm 2 . 1157J/mm as used in example 1 3 The hardness of the prepared laser cladding sample is improved compared with that of the prepared laser cladding sample, but the compressive strength, the deformation and the toughness are reduced due to the increase of the number of holes. Comparing the high-strength AlZnMgCu alloy (figure 8) prepared in the conventional way, the product of the compression strength and the deformation of the laser cladding sample is found to be close to that of the AlZnMgCu alloy which is difficult to carry out laser printing. The reduction in volume fraction of the precipitated phase at low energy density compared to example 3 results in a reduction in the potential difference between the second phase and the matrix and a slight increase in corrosion resistance, but more pores, and the corrosion rate is faster than that of the alloy sample of example 2, the corrosion potential is lower, and the corrosion current density is higher. But still more corrosion resistant than the corrosion performance of the other component alloys in table 5.
TABLE 6 laser energy Density of 694J/mm 3 Summary of average hardness, compressive properties, and toughness of time-laser clad aluminum alloy samples
Comparative example 1
The preparation of novel aluminum alloy samples by laser cladding process was essentially the same as steps (1) - (3) of example 2, except that a lower 496J/mm was used 3 Laser energy density is used for printing.
The performance test of the prepared laser cladding aluminum alloy sample comprises the verification of printability, the verification of organization gene phase, the verification of toughness and the like, and the verification method is the same as that of the example 2, and the verification result is as follows:
as shown in FIG. 3 (a), alMgZnCuErZr sample is on-laser cladding from laserThe optical energy density is 496J/mm 3 When the metallographic morphology of the laser cladding sample is adopted, the sample is molded at lower energy density, but crack defects are generated, and the density is reduced to 96.23%. Characterization of tissue gene phase revealed that at 496J/mm 3 The alloy sample structure prepared at laser energy density consists of 82vol.% alpha-Al, 13vol.% T-Mg 32 (AlZnCu) 49 、3.6vol.％Al 6 Mn、0.5vol.％Mg 2 Si and a small amount of Al 3 Zr、Al 3 The (Er, zr) key gene phase. The hardness of the sample in the stacking direction is tested by adopting an MHV 2000 digital Vickers microhardness tester, the loading load is 50g, the dwell time is 10s, and the result shows that the average hardness is 193HV, and the compression performance and the corrosion resistance of the sample are difficult to further measure due to crack generation of the sample.
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