CN113894177B - Strain metallurgy method for synthesizing multiphase alloy - Google Patents
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- RZJQYRCNDBMIAG-UHFFFAOYSA-N [Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Zn].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn] Chemical class [Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Zn].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn] RZJQYRCNDBMIAG-UHFFFAOYSA-N 0.000 description 2
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Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C11/00—Alloys based on lead
- C22C11/06—Alloys based on lead with tin as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C13/00—Alloys based on tin
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention relates to the field of metal materials, in particular to a strain metallurgy method for synthesizing multiphase alloy; the method comprises the following steps: 1) Determining the volume of the corresponding alloy element according to the proportion of each phase of the alloy; 2) Preparing a circular tube-shaped blank formed by combining all alloy element blocks; 3) The mandrel, the ring sleeve and the upper and lower pressure rings are adopted to respectively restrain the cylindrical surfaces and the end surfaces of the inner wall and the outer wall of the circular tubular blank, and high hydrostatic pressure is generated in the blank so as to cause the blank to generate primary plastic deformation; 4) Under the constant temperature and high hydrostatic pressure conditions of 0.20-0.90T m, torque is applied to the mandrel and the ring sleeve, circumferential shear deformation of the blank is realized, equivalent true strain reaches more than 1500, microscopic mixing of bulk alloy elements is realized, and the multiphase alloy with high metallurgical quality is formed. The alloy in the invention does not undergo the smelting and solidification processes of traditional metallurgy, and element segregation and the like caused by solidification phase change can not be avoided, so that the design of the multiphase alloy is liberated from the limitation of a phase diagram.
Description
Technical Field
The invention relates to the field of metal materials, in particular to a strain metallurgy method for synthesizing multiphase alloy.
Technical Field
The alloy refers to a substance formed by smelting, sintering or other methods of two or more metals and metal or metal and nonmetal raw materials. The constituent phases of the multiphase alloy according to the invention are pure metallic phases and/or solid solution phases. Alan Cottrell describes a multi-phase alloy as: the grains of two or more different phases are uniformly mixed and bonded to each other along their clearly narrow phase interfaces. When the cross section of a metallographic sample of a multiphase alloy is observed with an optical microscope, individual grains of the various constituent phases in the multiphase mixture can generally be easily seen. Their dimensions are typically on the order of 10 -5 to 10 -4 m (about several tens of mm) and often appear different colours after metallographic etching. [ Alan Cottrell, an Introduction to Metallurgy, THE INSTITUTE OF MATERIALS, london 1995, 204-206]. Homogeneous multiphase alloys are typically the products of thermodynamic phase change reactions such as eutectic, eutectoid, amplitude modulated decomposition or precipitation.
Two of the most common mainstream alloying formulations in the current metal material field are the melt alloying and the powder metallurgical alloying [ Habashi, F., alloys: preparation, properties, applications 1998: wiley-VCH ]. The earliest method for preparing the alloy is smelting metallurgy, which can be traced to the bronze age of 3000 years before the metric element, and bronze is prepared by smelting copper and tin. The technology for realizing alloying among elements in a molten state is convenient and efficient, gradually develops into a mainstream alloying method, and is widely used in industrial production and scientific research [ Stefanescu, D.M., ASM Handbook: volume 15: casting. 1988: ASM International ]. Therefore, the protection requirement of alloy melt and element segregation caused by phase change in smelting and casting alloy are also brought.
For example, pb-Sn is a typical eutectic system, and Pb-62% Sn (alloy components expressed in% by weight) which is an alloy of eutectic components is commonly used for solder and the like. Pb-Sn alloys are also classical superplastic alloys. Superplasticity requires a uniform fine equiaxed and stable grain structure. And (3) carrying out plastic processing on the Pb-Sn eutectic alloy after solidification, so as to obtain a biphase mixed structure with uniformly distributed lead-rich phases and tin-rich phases. The two phases are isolated from each other to inhibit the growth of crystal grains. This inhibition is most effective in alloys with equal volumes of the two phases because the separation between the two phases is maximized [Perumal R , Selzer M , Nestler B . Concurrent grain growth and coarsening of two-phase microstructures; large scale phase-field study. Computational Materials Science, 2018, 159:160-176]., however, when one uses a Pb-40% Sn sub-eutectoid alloy with equal volume fractions of the two phases to obtain superplasticity by casting and extrusion, the superplasticity elongation is only 400%, which is significantly lower than 600%[Ha, Y.W. Chang, Effects of temperature and microstructure on the superplasticity in microduplex Pb-Sn alloys, Mater. Sci. Forum 357-359 (2001) 159-164]. of eutectic alloys Pb-62% Sn with unequal volume fractions of the two phases under the same conditions, because a large amount of lead-rich first eutectic phase is first precipitated from the melt when the alloy with hypoeutectic composition solidifies, as shown in FIG. 1. The proportion of the eutectic lead-rich phase of the alloy with Pb-40% Sn is estimated to be about 50% of the weight of the whole alloy melt according to the phase diagram. The solidification process, in which about 50% of the remaining melt solidifies into a homogeneous biphasic structure [D.R. Askland, W.J. Wright. The Science and Engineering of Materials, Cengage Learning, (2014) 398]. by eutectic reaction after cooling to the eutectic temperature, produces a substantial separation of the chemical components of the eutectic lead-rich phase and the eutectic biphasic phase. This results in significant phase distribution non-uniformity compared to the eutectic bi-phase, which is a uniform tissue mixture, causing severe damage to the tissue uniformity conditions required for superplasticity.
On the other hand, powder metallurgy has been rapidly developed in the 19 th century [ Upadhyaya, g.s., powder Metallurgy technology, cambridge International Science Publishing,1997], and as a solid-state alloying method, powder metallurgy can produce an alloy of an immiscible system (alloy system with positive heat of mixing) which cannot be produced by smelting metallurgy, as a new alloy production method. The alloy prepared by this method generally suffers from difficulties in 100% densification and inadequate metallurgical bonding between powder particles, which can have a significant negative impact [G.S. Upadhyaya. Powder Metallurgy Technology, Cambridge International Science Publishing, (1997) 143-144]. on the overall mechanical properties of the alloy, particularly on plasticity and toughness, and for this purpose, standard tensile properties tests are used, if necessary, on the powder metallurgical product to evaluate its overall mechanical properties and metallurgical quality [P. Samal, J. Newkirk. Materials standards and test method standards for powder metallurgy,. ASM Handbook, 7, ASM International (2015) 45-51].
In recent years, a new class of severe plastic deformation processes capable of achieving circumferential shear deformation of tubular billets under high hydrostatic pressure has been attracting attention [ J.T. Wang, et al Scripta Mater 67 (2012) 810]. The main inventor of the present invention proposes a specific implementation manner of the process in 2011, which is called a tube high-pressure shearing (t-HPS) method and a device thereof (authorized, 201110030903.0, 201110291933.7), and the process has successfully achieved submicron grain structure of materials such as pure aluminum, pure copper, IF steel, and the like, and obtains pure metal with an ultra-fine grain structure. Later developed single-process processing methods (201510918670.6) for multi-layer metal composites were also patented. At present, all the technologies only carry out plastic processing on the existing metal or alloy to refine the grain structure or realize the layered composition of different metals and alloys.
Disclosure of Invention
The purpose of the invention is that: the strain metallurgy method for synthesizing the multiphase alloy is characterized in that the method directly synthesizes and prepares the multiphase alloy block with high metallurgical quality from the alloy element solid block without a melting and mixing process and a solidification process, and the defects of element segregation and the like caused by phase change in the solidification process are avoided, so that the component design of the uniform multiphase alloy is liberated from the limitation of a phase diagram.
In order to solve the technical problems, the invention adopts the following technical scheme:
A strain metallurgy method of synthesizing a multi-phase alloy, the method comprising the steps of:
1) Component design is carried out according to the performance requirement and the structure requirement of the alloy, and then the volume ratio of corresponding alloy elements is calculated and determined according to the proportion of each alloy phase;
2) Preparing a circular tube-shaped combined blank formed by combining blocks of all alloy elements according to the volume ratio of all alloy elements;
3) The mandrel and the annular sleeve are adopted to respectively restrict the cylindrical surfaces of the inner wall and the outer wall of the circular tube-shaped combined blank, and the pressure ring is used to apply axial load to the two annular end surfaces of the circular tube-shaped combined blank, so that 1 GPa-30 GPa hydrostatic pressure is generated inside the circular tube-shaped combined blank, and the circular tube-shaped combined blank is subjected to primary plastic deformation; the gaps among the element blocks are closed to achieve the effect of approaching cold welding, and environmental gases such as air and the like are prevented from entering the combined blank pollution materials through the combined/spliced gaps;
4) Placing the system subjected to the preliminary plastic deformation in the step 3) in a constant temperature environment with the temperature of 0.20-0.90T m, or keeping the temperature of the circular tube-shaped combined blank constant; at least one of the mandrel and collar is simultaneously torqued so that it produces circumferential shear and equivalent true strain reaches above 1500.
The temperature is controlled in the range of 0.20-0.90T m, because the deformation capability of each element is insufficient due to the fact that the temperature is too low, the elements cannot be mixed by deformation without breaking; too high a temperature oxidizes severely and at the same time some elements react easily to form compounds, which affect the synthesis of multiphase alloys with pure metals or solid solutions as constituent phases.
The circumferential shear deformation of the blank is achieved while maintaining the above-mentioned temperature and internal hydrostatic pressure of the round tubular composite blank. With the increase of the deformation, the contact surfaces among the alloy element blocks gradually realize metallurgical bonding to form phase interfaces, and the phase interfaces are unstable under the shearing action to cause solid-state mixing among elements. Under the combined action of temperature and pressure, when the equivalent true strain of circumferential shearing reaches more than 1500, the alloy phases formed by all alloy elements are mixed to a statistically uniform degree, a multiphase alloy is formed, and the geometric dimension of each alloy phase (pure metal or solid solution) reaches less than tens of micrometers. Thus, each alloy element is synthesized into multiphase alloy by solid state deformation processing of independent blocks, and has physical and mechanical properties of multiphase alloy.
The strain metallurgy method for preparing and synthesizing the multiphase alloy breaks through the restriction of first eutectic (first eutectoid) phase precipitation on the uniformity of the alloy in the alloying technical route of alloy smelting and solidification, and obtains high performances such as large superplasticity which cannot be obtained by the conventional smelting metallurgy method.
Further, the combination form of the circular tube-shaped combined blank comprises a spliced circular tube and a concentric circular tube,
The spliced round pipe is formed by splicing straight strips with circular arc sections in cross section by prefabricating alloy element blocks, the ratio of the central angles of the circular arc sections corresponding to the alloy elements is equal to the volume ratio of alloy design, and the sum of the central angles of the circular arc sections corresponding to all the alloy elements is equal to 2 pi;
The concentric circular tubes are formed by a plurality of circular tubes which can be mutually nested into a combined concentric circular tube, each circular tube is an element circular tube which is prepared into a high-uniformity alloy element block body, and the diameter and the wall thickness of the element circular tube are calculated and determined by the corresponding volume ratio of the element in the alloy.
Furthermore, the arc section or the element circular tube prefabricated and formed by each alloy element block is subjected to surface treatment for removing pollutants and an oxidation layer before assembling the tissues, and the joint surface are in close contact in the assembling and combining process.
Further, each alloy element block has a size of not less than 1mm in three dimensions.
Further, the torque applied in the step 4) is torque in the circumferential direction for providing the mandrel, and the ring sleeve is fixed.
Further, the torque applied in the step 4) is a torque for fixing the mandrel and providing the circumferential torque to the ring sleeve.
Further, the torque applied in the step 4) is torque which simultaneously provides opposite directions for the mandrel and the ring sleeve, so that the mandrel and the ring sleeve relatively rotate around the central axis of the circular tubular blank.
The technical scheme of the invention has the beneficial effects that:
1. The multiphase alloy is directly synthesized by the alloy element blocks, the alloy is formed by micro-mixing, interfacial metallurgical bonding and metallurgical reaction among alloy elements through severe shearing plastic deformation, and the designed multiphase alloy can be synthesized by only one working procedure after the round tubular combined blank is finished.
2. The multiphase alloy in the invention does not need to pass through smelting and solidification processes like the traditional metallurgical process, so that the defects of element segregation and the like caused by phase change in the solidification process are avoided, and the composition design of the uniform multiphase alloy is released from the limitation of a phase diagram.
3. The strain metallurgy synthesis method of the multiphase alloy is suitable for an alloy system which is insoluble (the mixed heat is positive).
4. According to the strain metallurgy synthesis method of the multiphase alloy, liquid processes such as metal melt and the like are not needed, and the behaviors such as burning loss and oxidization related to high-temperature melt are not generated; on the other hand, in the powder metallurgy alloying process, pollution caused by high activity of metal powder and adverse effect [P. Samal, J. Newkirk. Materials standards and test method standards for powder metallurgy,. ASM Handbook, 7, ASM International (2015) 45-51], of powder metallurgy residual pore on alloy performance, especially on plasticity and toughness of materials [G.S. Upadhyaya. Powder Metallurgy Technology, Cambridge International Science Publishing, (1997) 143-144].
The multiphase alloy block synthesized by the invention has high metallurgical quality and can obtain excellent mechanical properties. As shown in example 2 and FIG. 11, the multi-phase Pb-40% Sn alloy synthesized according to the present invention has a tensile elongation of 1870% at room temperature at an initial strain rate of 1.0X10 -3s-1. This elongation is more than three times the highest elongation of 600% obtained in Pb-Sn alloys based on the smelting casting and then processing.
Drawings
FIG. 1 is a schematic diagram showing Pb-Sn equilibrium phase diagram, and solidification process and solidification structure of hypoeutectic alloy (Pb-30% Sn) [D.R. Askland, W.J. Wright. The Science and Engineering of Materials, Cengage Learning, (2014) 398].
FIG. 2 shows a combined round tube blank formed by splicing two semicircular tubes of two alloy elements. 21. 22 are respectively A, B semi-circular tubes of two alloy elements.
Fig. 3 is a composite round tube blank composed of concentric circles of two alloying elements. 31. 32 are round tubes of A, B alloy elements respectively.
Fig. 4 shows a combined round tube blank formed by splicing straight strips of five alloy elements with circular arc sections in cross section. 41. 42, 43, 44, 45 are straight bars of A, B, C, D, E alloying elements with circular arc sections in cross section respectively. The sum of central angles of the arc sections corresponding to the five elements is just 2 pi.
Fig. 5 is a composite round tube blank composed of concentric circles of three alloying elements. 51. 52, 53 are round tubes of three alloying elements respectively A, B, C.
FIG. 6 is a schematic illustration of t-HPS processing of a double-split round tube of two alloying elements. Wherein, 1-dabber, 2-lower clamping ring, 3-tubular blank, 4-upper clamping ring, 5-ring cover.
FIG. 7 is a schematic diagram of a dual phase alloy tube directly strain metallurgically synthesized from two alloy element blocks.
Fig. 8 is a graph of EBSD (back scattered electron diffraction) phase composition of a composite biphase alloy of two phases fully mixed and synthesized by turbulence on the cross section of a concentric circular tube combined cylindrical sample with a volume ratio of lead (light)/tin (dark) of 1:1 after 30 relative rotations of the inner and outer walls (corresponding to equivalent strain 1200).
Fig. 9 is a graph of EBSD (backscattered electron diffraction) phase composition of a composite biphasic alloy of two phases fully mixed and synthesized by turbulence on the cross section of a concentric circular tube combined cylindrical sample with a volume ratio of lead (light)/tin (dark) of 1:1 after 40 turns of relative rotation of the inner and outer walls (corresponding to equivalent true strain 1600).
FIGS. 10a and b are graphs of the composition of the EBSD (back scattered electron diffraction) phase and the orientation diagram (IPF) of an elemental bulk strain metallurgically synthesized eutectic alloy with a lead (bright)/tin (dark) volume ratio of 28:72 (Pb-62% Sn eutectic composition). FIGS. 10c and d are diagrams of the composition of the EBSD (back scattered electron diffraction) phase and the orientation diagram (IPF) of an elemental bulk strain metallurgically synthesized eutectic alloy with a volume ratio of lead (light)/tin (dark) of 1:1 (Pb-40% Sn hypoeutectic composition).
FIG. 11 corresponds to the engineering stress-engineering strain curves of the two strain metallurgically synthesized Pb-62% Sn alloys (solid dotted data points) and Pb-40% Sn alloys (hollow dotted data points) of FIG. 10 drawn at room temperature at an initial strain rate of 1.0X10 -3s-1. The inset is a photograph of the sample before stretching and of the sample after stretching of both alloys.
Detailed Description
The strain metallurgical synthesis method of the multiphase alloy of the present invention is further described below in connection with the specific embodiments.
Example 1
Raw materials in this example: alloy element lead and tin blocks.
A method of strain metallurgical synthesis of a multiphase alloy comprising the steps of:
(1) Firstly, alloy design is carried out according to the performance requirement and the structure requirement of the alloy, and the volume ratio of corresponding alloy elements is mainly calculated and determined according to the proportion of each alloy phase. The biphase alloy to be synthesized in the embodiment is Pb-62% Sn biphase alloy with eutectic composition, and the volume ratio of the two alloying elements of lead/tin is 28:72;
(2) Preparing a circular tube-shaped combined blank (a workpiece for t-HPS processing) formed by combining the element blocks according to the volume ratio of each alloy element;
as shown in fig. 2-7, there may be two combinations of workpieces:
The method comprises the steps of splicing round pipes, namely, prefabricating each alloy element block into a straight strip with a circular arc section in the cross section shape, wherein the ratio of the central angles of the circular arc sections corresponding to each alloy element is equal to the volume ratio of alloy design, and the sum of the central angles of the circular arc sections corresponding to all alloy elements is equal to 2 pi (the circular arc sections corresponding to all alloy elements are spliced together to just form a combined round pipe);
Concentric circular tubes, the alloy element blocks are prefabricated into element circular tubes with uniform height and determined by the volume ratio of the elements in the alloy, and the inner diameter and the outer diameter of each circular tube can be mutually nested into a combined concentric circular tube;
all of these alloying elements are carefully polished, surface treated to remove contaminants and oxide layers prior to joining the structure. The joint and the joint surface are in close contact in the process of splicing and combining, and a gap is not reserved;
in the embodiment, a spliced circular tube with two alloy element circular arc sections is adopted as a blank, the central angles corresponding to the lead/tin circular arc sections are 101 degrees/259 degrees respectively, and the wall thickness of the spliced circular tube is 2 mm, and the height is 15 mm;
(3) The mandrel 1 and the ring sleeve 5 are adopted to respectively restrain the cylindrical surfaces of the inner wall and the outer wall of the split circular tube blank, and the pressure rings (comprising the upper pressure ring 4 and the lower pressure ring 2) are used to apply axial load to the two annular end surfaces of the circular tube-shaped combined blank, so that the full restraint of the circular tube-shaped combined blank is realized;
under the combined action of the axial pressure of the pressure rings 2 and 4 and the restraint of the mandrel 1 and the ring sleeve 5, generating hydrostatic pressure of 1.2 GPa in the circular tube-shaped combined blank; meanwhile, the round tubular combined blank is subjected to preliminary (compression) plastic deformation, so that gaps among element blocks are closed to achieve the effect of approaching cold welding, and environmental gases such as air are prevented from entering the combined blank through the combined/spliced gaps;
(4) The above-mentioned tubular composite material, the mandrel 1 for restraining the inner and outer cylinders, the collar 5, the pressure ring for restraining the end, and the like were maintained in a constant temperature environment of 0.58T m (T m is the melting point 505.06K of tin having a low melting point in lead and tin) according to the characteristic that the plastic deformation ability of each alloy element changes with temperature.
(5) Under the conditions of constant temperature of 0.58T m(Tm and tin melting point) and hydrostatic pressure of 1.2 GPa, the fixed mandrel 1 rotates the ring sleeve 5 to perform circumferential high-pressure shearing, the plastic deformation reaches equivalent true strain 2000, and the designed Pb-62% Sn eutectic component dual-phase alloy is synthesized. In the synthesized dual phase alloy, the lead-rich phase and the tin-rich phase are uniformly distributed, as shown in fig. 10 a. The average grain size of the two phases reached 1.1.+ -. 0.1mm as shown in FIG. 10 b. The engineering stress-engineering strain curve of the Pb-62% Sn alloy stretched at room temperature at an initial strain rate of 1.0X10 -3s-1 is shown as solid circle data points in FIG. 11, and the elongation at stretching reaches 670%. This elongation is equal to 600% of the highest elongation obtained in Pb-62% Sn eutectic alloys based on the melting casting and then plastic working treatment [T.K. Ha, Y.W. Chang, Effects of temperature and microstructure on the superplasticity in microduplex Pb-Sn alloys, Mater. Sci. Forum 357-359 (2001) 159-164].
The inset in fig. 11 gives photographs of the corresponding alloy before and after stretching.
In the embodiment, the eutectic component Pb-62% Sn block superplastic alloy synthesized by directly carrying out t-HPS large plastic deformation on block lead and tin has the elongation not lower than the highest value of the elongation of a sample prepared by casting and alloying with the same component, and the observation and analysis on the microstructure of the alloy show that the alloy reaches a high metallurgical quality level.
Example 2-example 4 parameters of the target alloy, the initial bulk alloy element volume ratio, the constant temperature during processing, the constant hydrostatic pressure, and the equivalent strain amount of the circumferential high pressure shear are shown in table 1, and other process operations are the same as in example 1.
TABLE 1
Example 2
In this example, under the conditions of constant temperature 0.58T m(Tm being the melting point of tin) and constant pressure 1.2 GPa, the circumferential high-pressure shear is performed, and the plastic deformation reaches equivalent true strain 1600. In the synthesized Pb-40% Sn hypoeutectic composition dual-phase alloy, the lead-rich phase and the tin-rich phase are uniformly distributed, as shown in FIG. 10 c. The average grain size of the two phases reached 1.0.+ -. 0.1mm as shown in FIG. 10 d. The engineering stress-engineering strain curve of the Pb-40% Sn alloy stretched at room temperature at an initial strain rate of 1.0X10 -3s-1 is shown as open circle data points in FIG. 11, and the elongation at stretching reaches 1870%. This elongation is more than three times the highest elongation of 600% obtained in Pb-Sn alloys based on the smelting casting and then processing [T.K. Ha, Y.W. Chang, Effects of temperature and microstructure on the superplasticity in microduplex Pb-Sn alloys, Mater. Sci. Forum 357-359 (2001) 159-164].
The inset in fig. 11 gives photographs of the corresponding alloy before and after stretching. Therefore, the technical route of synthesizing the multiphase alloy from the alloy element solid block through strain metallurgy is shown, the limitation of the uniformity of the alloy due to the first eutectic phase precipitation in the technical route of alloy smelting and solidification shown in fig. 1 is broken through, the composition design of the alloy has a larger degree of freedom, and a technical approach is provided for designing and preparing the alloy with better performance (such as superplasticity in the embodiment).
Example 3
In this example, a Pb-40% Sn hypoeutectic composition dual-phase alloy was synthesized by strain metallurgy, and the lead-rich phase and the tin-rich phase were distributed relatively uniformly, but there was still an indication of preferential distribution in the circumferential direction (transverse direction in FIG. 8), as shown in FIG. 8. The average grain size of the two phases reaches 2.1+/-0.3 mm.
Example 4
In this example, a Pb-40% Sn hypoeutectic composition two-phase alloy was synthesized by strain metallurgy, and the lead-rich phase and the tin-rich phase were uniformly distributed, and no sign of preferential distribution in the circumferential direction (the lateral direction in FIG. 9) was recognized, as shown in FIG. 9. The average grain size of the two phases reaches 1.9+/-0.3 mm.
The lead and tin of each alloy element block and the lead-tin alloy synthesized by the lead and tin are only one applicable example, and the synthesis method of the invention is also applicable to other materials, such as aluminum, copper, nickel, niobium, iron, magnesium, indium, lithium and other element blocks, and the like, and the alloy is synthesized into a dual-phase or multi-phase alloy. Figures 2-5 of the present invention provide schematic diagrams of two blank combinations of split round tubes and concentric round tubes, and only the combined blank forms are schematically illustrated. The kinds of alloying elements used in synthesizing a multiphase alloy in practice are not limited to 2, 3, 5 kinds given in these schematic diagrams, but 2 kinds or more as required according to the alloy design.
It will be evident to those skilled in the art that the invention is not limited to the details of the foregoing illustrative examples and that the present invention may be embodied in other specific forms without departing from the spirit or essential characteristics thereof. The present embodiments are therefore to be considered in all respects as illustrative and not restrictive, the scope of the invention being indicated by the appended claims rather than by the foregoing description, and all changes which come within the meaning and range of equivalency of the claims are therefore intended to be embraced therein.
Furthermore, it should be understood that while the present description describes embodiments, not every embodiment is presented by way of example only, and that this description is provided for clarity only, and that the present disclosure is not limited to the embodiments described in the figures, as such, and that the embodiments described in the examples may be combined in any suitable manner to form other embodiments that will be apparent to those of skill in the art.
Claims (7)
1. A strain metallurgy method for synthesizing a multiphase alloy, characterized by: the method comprises the following steps:
1) Component design is carried out according to the performance requirement and the structure requirement of the alloy, and the volume ratio of corresponding alloy elements is calculated and determined according to the proportion of each alloy phase;
2) Preparing a circular tube-shaped combined blank formed by combining blocks of all alloy elements according to the volume ratio of all alloy elements;
3) The mandrel and the annular sleeve are adopted to respectively restrict the cylindrical surfaces of the inner wall and the outer wall of the circular tube-shaped combined blank, and the pressure ring is used to apply axial load to the two annular end surfaces of the circular tube-shaped combined blank, so that 1 GPa-30 GPa hydrostatic pressure is generated inside the circular tube-shaped combined blank, and the circular tube-shaped combined blank is subjected to primary plastic deformation;
4) Placing the system subjected to the preliminary plastic deformation in the step 3) in a constant temperature environment with the temperature of 0.20-0.90T m, wherein T m is the melting point of a component with low melting point in the system, or keeping the temperature of the circular-tube-shaped combined blank constant; at the same time, a driving torque is applied to at least one of the mandrel and the collar, so that the mandrel and the collar generate circumferential shear deformation and equivalent true strain reaches more than 1500.
2. A strain metallurgy method for synthesizing a multi-phase alloy according to claim 1, wherein: the combination form of the circular tube-shaped combined blank comprises a spliced circular tube and a concentric circular tube,
The spliced round pipe is formed by splicing straight strips with circular arc sections in cross section by prefabricating alloy element blocks, the ratio of the central angles of the circular arc sections corresponding to the alloy elements is equal to the designed volume ratio of the alloy components, and the sum of the central angles of the circular arc sections corresponding to all the alloy elements is equal to 2 pi;
the concentric circular tubes are formed by a plurality of circular tubes which can be mutually nested into a combined concentric tube, each circular tube is an element circular tube which is prepared for each alloy element block body and has uniform height, and the diameter and the wall thickness are calculated and determined by the corresponding volume ratio of the element in the alloy.
3. A strain metallurgy method for synthesizing a multi-phase alloy according to claim 1, wherein: the arc section or the element circular tube prefabricated and formed by each alloy element block is subjected to surface treatment for removing pollutants and oxide layers before assembling the tissues, and joints and joint surfaces are in close contact in the assembling and combining process.
4. A strain metallurgy method for synthesizing a multi-phase alloy according to claim 1, wherein: the size of each alloy element block in three dimensions is not less than 1mm.
5. A strain metallurgy method for synthesizing a multi-phase alloy according to claim 1, wherein: the torque applied in the step 4) is torque in the circumferential direction for providing the mandrel, and the ring sleeve is fixed.
6. A strain metallurgy method for synthesizing a multi-phase alloy according to claim 1, wherein: the torque applied in step 4) is a fixed mandrel and provides circumferential torque to the collar.
7. A strain metallurgy method for synthesizing a multi-phase alloy according to claim 1, wherein: and in the step 4), torque is applied to simultaneously provide torque in opposite directions for the mandrel and the ring sleeve, so that the mandrel and the ring sleeve relatively rotate around the central axis of the circular tubular blank.
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