CN113894177A - Strain metallurgy method for synthesizing multiphase alloy - Google Patents
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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
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- 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
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- 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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Abstract
The invention relates to the field of metal materials, in particular to a strain metallurgy method for synthesizing a 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 tubular blank composed of alloy element blocks; 3) respectively constraining the cylindrical surfaces and the end surfaces of the inner wall and the outer wall of the circular tubular blank by adopting a mandrel, a ring sleeve and an upper pressure ring and a lower pressure ring, and generating high hydrostatic pressure in the blank to generate preliminary plastic deformation; 4) in the range of 0.20 to 0.90T mUnder the conditions of constant temperature and high hydrostatic pressure, the core shaft and the ring sleeve are applied with torque, the circumferential shear deformation of the blank is realized, the equivalent true strain reaches more than 1500, the block alloy elements are enabled to realize micro-mixing,forming a high metallurgical quality multi-phase alloy. The alloy does not pass through the smelting and solidification processes of traditional metallurgy, does not cause element segregation and the like due to solidification phase change, and relieves the design of the multiphase alloy 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 a multi-phase alloy.
Technical Field
An alloy refers to a material made by melting, sintering, or otherwise combining two or more metals with metals or metals and non-metallic materials. The composition phases of the multi-phase alloy according to the present invention are pure metal phases and/or solid solution phases. Alan Cottrell describes a multiphase alloy as: a multiphase mixture in which two or more kinds of crystal grains of different phases are uniformly mixed and bonded to each other along a sharp narrow phase boundary. When a cross section of a metallographic sample of a multiphase alloy is observed with an optical microscope, individual grains of each constituent phase in the multiphase mixture can be easily seen in general. They are typically 10 in size-5To 10-4m (about several tens of μm) and generally exhibit different colors after metallographic etching. [ Alan Cottrell, An Introduction to metals, THE inertia OF MATERIALS, London 1995,204-]. Homogeneous multiphase alloys are generally the products of thermodynamic phase change reactions such as eutectic, eutectoid, spinodal decomposition or precipitation.
Two of the most common major alloying methods currently used in the field of metallic materials are melt alloying and powder metallurgy alloying [ Habashi, F., Alloys: Preparation, Properties, applications.1998: Wiley-VCH ]. The earliest method for preparing alloy was smelting metallurgy, which dates back to the bronze era 3000 b.c., bronze is made by smelting copper and tin. The technology for realizing alloying between elements in a molten state is convenient and efficient, is gradually developed 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 alloy melt protection requirement, element segregation caused by phase change in the smelting and casting alloy and the like are brought.
For example, the Pb-Sn system is a typical eutectic system, and an alloy of eutectic composition, Pb-62% Sn (all the alloy compositions expressed by% are in weight percent) 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. After solidification, the Pb-Sn eutectic alloy is subjected to plastic processing, and a two-phase mixed structure with uniformly distributed lead-rich phase and tin-rich phase can be obtained. The two phases are isolated from each other, and the growth of crystal grains is inhibited. This inhibition is most effective in two-phase alloys with equal volume, because the isolation between the two phases is maximized when the two phases are equal in volume [ Perual R, Selzer M, Nestler B. Current grain growth and correlation of two-phase microstructures; large scale phase-field study. computerized Materials Science,2018,159: 160-. However, when one obtains superplasticity by casting and extruding a Pb-40% Sn hypoeutectoid alloy with equal volume fraction of two phases, the superplasticity elongation is only 400%, which is significantly lower than 600% of the Pb-62% Sn eutectic alloy with unequal volume fraction of two phases under the same conditions [ Ha, Y.W.Chang, Effects of temperature and microstructure on the superplastification in microduct Pb-Sn alloys, Mater.Sci.Forum 357-359(2001)159-164 ]. This is because, when the alloy of hypoeutectic composition is solidified, a large amount of lead-rich eutectic phase is precipitated from the melt as shown in fig. 1. The proportion of pre-eutectic lead-rich phase of the alloy having a composition of Pb-40% Sn was estimated to be about 50% by weight of the entire alloy melt based on the phase diagram. After cooling to the eutectic temperature, the remaining about 50% of the melt solidifies into a homogeneous biphasic structure by eutectic reaction [ d.r. asskland, w.j.wright. the Science and Engineering of Materials, center leiarning, (2014)398 ]. The solidification process produces a large amount of separation of the pre-eutectic lead-rich phase from the chemical constituents of the eutectic two-phase. This results in significant phase distribution non-uniformity, and severe damage to the tissue homogeneity conditions required for superplasticity, as compared to eutectic biphasic with homogeneous tissue mixing.
On the other hand, Powder Metallurgy has rapidly developed in the 19 th century [ updhyaya, g.s., Powder Metallurgy technology, cambridge International Science Publishing, 1997], and as a solid-state alloying method, Powder Metallurgy can prepare an alloy of an immiscible system (alloy system with positive heat of mixing) that cannot be prepared by smelting Metallurgy, becoming a new alloy preparation method. Alloys prepared by this method often suffer from difficulties with 100% densification, inadequate metallurgical bonding between powder particles, etc., which have a significant negative impact on the overall mechanical properties of the alloy, particularly plasticity and toughness [ G.S. Updhyaya. powder Metallurgy Technology, Cambridge International Science Publishing, (1997)143- "144 ]. To this end, the powder metallurgy products are evaluated, if necessary, for their combination of mechanical properties and metallurgical quality using standard tensile property tests [ P.Samal, J.Newkirk.materials standards and test methods for powder metallurgy,. ASM Handbook,7, ASM International (2015)45-51 ].
In recent years, a new process of severe plastic deformation capable of realizing circumferential shear deformation of a tubular blank under the action of high hydrostatic pressure is attracting attention [ j.t.wang, et al.script mater.67(2012)810 ]. The main inventor of the present invention has proposed a specific implementation manner of the process in 2011, which is called a tube high-pressure shear deformation method (t-HPS method for short) and a device thereof (authorized, 201110030903.0, 201110291933.7), at present, the process has successfully achieved submicron crystal grain structures of materials such as pure aluminum, pure copper, IF steel, and the like, and pure metals with ultra-fine crystal structures are obtained. Later developed single-pass processing of multilayer metal composites (201510918670.6) patents were also granted. At present, all of these techniques are only to perform plastic working on existing metals or alloys to refine their grain structures or to laminate different metals or alloys.
Disclosure of Invention
The purpose of the invention is: the method has the advantages that the method does not need a melting and mixing process and a solidification process, directly synthesizes and prepares the multiphase alloy block with high metallurgical quality from the alloy element solid block, and does not have the defects of element segregation and the like caused by phase change in the solidification process, thereby liberating the component design of the uniform multiphase alloy from the limitation of a phase diagram.
In order to solve the technical problems, the technical scheme adopted by the invention is as follows:
a strain metallurgy method of synthesizing a multi-phase alloy, the method comprising the steps of:
1) designing components according to the performance requirements and the structure requirements of the alloy, and then calculating and determining the volume ratio of corresponding alloy elements according to the proportion of each alloy phase;
2) preparing a circular tube-shaped combined blank combined by blocks of the alloy elements according to the volume ratio of the alloy elements;
3) respectively constraining the inner wall cylindrical surface and the outer wall cylindrical surface of the circular tubular combined blank by adopting a mandrel and a ring sleeve, and applying axial load to two annular end surfaces of the circular tubular combined blank by using a pressure ring so as to generate 1 GPa-30 GPa hydrostatic pressure in the circular tubular combined blank and generate primary plastic deformation of the circular tubular combined blank; the gaps between the element blocks are closed to achieve the effect close to cold welding, and environmental gases such as air and the like are inhibited from entering the combined blank polluted materials through the combined/spliced gaps;
4) placing the system subjected to the preliminary plastic deformation in the step 3) at the temperature of 0.20-0.90TmOr only keeping the circular tube-shaped combined blank at the constant temperature; and simultaneously applying torque to at least one of the mandrel and the collar to generate circumferential shear and enable equivalent true strain to be more than 1500.
Controlling the temperature to 0.20-0.90TmRange, because the deformability of the elements is insufficient at too low a temperature, there is no way to achieve element mixing by deformation without fracture; the temperature is too high, the oxidation is serious, and simultaneously, some elements are easy to react to form compounds, so that the synthesis of the multiphase alloy taking pure metal or solid solution as a component phase is influenced.
Circumferential shear deformation of the round tubular composite billet is achieved while maintaining the above-mentioned temperature and internal hydrostatic pressure of the billet. Along with the increase of the deformation, the contact surface between the alloy element blocks gradually realizes metallurgical bonding to form a phase interface, and the phase interface is destabilized under the shearing action to cause solid-state mixing between the 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 the alloy elements are mixed to a statistically uniform degree to form a multi-phase alloy, and the geometric dimension of each alloy phase (pure metal or solid solution) reaches less than tens of microns. Therefore, each alloy element is synthesized into the multiphase alloy through solid state deformation processing from independent blocks, and has the physical and mechanical properties of the multiphase alloy.
The strain metallurgy method for preparing and synthesizing the multiphase alloy breaks through the restriction of the precipitation of eutectic (pro-eutectoid) phase in the alloying technical route of alloy smelting and solidification on the uniformity of the alloy, and obtains high performance such as large superplasticity and the like which cannot be obtained by the conventional smelting metallurgy method.
Furthermore, the combination form of the circular tube-shaped combined blank comprises a splicing circular tube and a concentric circular tube,
the spliced circular tube is formed by splicing straight strips of which the cross sections are arc sections and are prefabricated from alloy element blocks, the ratio of the central angles of the arc sections corresponding to the alloy elements is equal to the designed volume ratio of the alloy, and the sum of the central angles of the arc sections corresponding to all the alloy elements is equal to 2 pi;
the concentric circular tubes are composed of a plurality of circular tubes, the inner diameter and the outer diameter of which can be mutually nested into a combined concentric circular tube, and each circular tube is an element circular tube which is prefabricated into each alloy element block body with uniform height but the diameter and the wall thickness of which are determined by calculating the corresponding volume ratio of the element in the alloy.
Further, the arc sections or the element round pipes prefabricated and formed by the alloy element blocks are subjected to surface treatment for removing pollutants and oxide layers before assembling organization, and seams are in close contact with the binding surfaces in the splicing and combining process.
Further, the size of each alloy element block in three dimensions is not less than 1 mm.
Further, the torque applied in the step 4) is used for providing the torque in the circumferential direction for the mandrel, and the ring sleeve is fixed.
Further, the step 4) of applying torque to fix the mandrel and provide circumferential torque to the ring sleeve.
Further, the torque applied in the step 4) is used for simultaneously providing opposite-direction torque to the mandrel and the ring sleeve, so that the mandrel and the ring sleeve can rotate relatively around the central axis of the round tubular blank.
The technical scheme adopted by the invention has the beneficial effects that:
1. the multiphase alloy is directly synthesized by the alloy element blocks, the micromixing, the interface metallurgical bonding and the metallurgical reaction among the alloy elements are realized through violent shearing plastic deformation to form the alloy, the designed multiphase alloy can be synthesized only by one process after the circular tubular combined blank is finished, and the alloy has the advantages of simple synthesis and preparation process and high production efficiency.
2. The multiphase alloy does not need to be smelted and solidified like the traditional metallurgical process, so that the defects of element segregation and the like caused by phase transformation in the solidification process can not be generated, and the composition design of the uniform multiphase alloy is liberated from the limitation of a phase diagram.
3. The strain metallurgy synthesis method of the multiphase alloy is suitable for an immiscible (positive mixing heat) alloy system.
4. The strain metallurgy synthesis method of the multi-phase alloy does not need to pass through liquid processes such as metal melt and the like, so that the behaviors such as loss of ignition, oxidation and the like related to high-temperature melt are not generated; on the other hand, in the powder Metallurgy alloying process, contamination caused by high activity of the metal powder and adverse effect of the powder Metallurgy residual porosity on the alloying performance [ P.Samal, J.New kirk.materials standards and test methods standards for powder Metallurgy metals,. ASM Handbook,7, ASM International (2015)45-51], particularly on the plasticity and toughness of the material [ G.S.Updhyaya.powder Technology, Cambridge International Science Publishing, (1997)143- "144 ].
The multi-phase alloy block synthesized by the method has high metallurgical quality and can obtain excellent mechanical properties. As shown in example 2 and FIG. 11, the synthesized multi-phase Pb-40% Sn alloy of the present invention was 1.0X 10 at room temperature-3s-1The initial strain rate of (2) is 1870% for tensile elongation. This elongation is more than three times the highest elongation 600% obtained on the basis of a Pb-Sn alloy that is melt cast and then processed.
Drawings
FIG. 1 is a Pb-Sn equilibrium phase diagram and a schematic diagram of solidification process and solidification structure of hypoeutectic alloy (Pb-30% Sn) [ D.R. Askland, W.J. Wright, the Science and Engineering of Materials, center Learning, (2014)398 ].
FIG. 2 is a blank for combining two semi-circular tubes of two alloy elements. 21. 22 are respectively half-round tubes of A, B 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 two alloying elements respectively.
Fig. 4 is a combined circular tube blank formed by splicing straight strips of five alloy elements with circular arc sections in cross section. 41. 42, 43, 44 and 45 are respectively straight strips of A, B, C, D, E alloy elements with the cross sections of circular arc sections. 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, 53A, B, C respectively.
FIG. 6 is a schematic representation of a two alloy element double-barrelled tube subjected to t-HPS processing. The device comprises a mandrel 1, a lower pressing ring 2, a tubular blank 3, an upper pressing ring 4 and a ring sleeve 5.
FIG. 7 is a schematic view of a dual phase alloy tube directly strain metallurgically synthesized from two bulk alloying elements.
Fig. 8 is a diagram showing EBSD (back scattered electron diffraction) phase composition of a two-phase fully mixed, synthesized two-phase alloy, in which a concentric circular tube/tin (dark) volume ratio of 1:1 is combined with a cylindrical sample, and after the inner and outer walls are relatively rotated for 30 turns (corresponding to equivalent true strain 1200), the two phases are completely mixed due to turbulence on the cross section.
Fig. 9 is a diagram showing EBSD (back scattered electron diffraction) phase composition of a two-phase fully mixed, synthesized two-phase alloy, resulting from turbulence on the cross section of a concentric circular tube-combined cylindrical sample having a lead (light)/tin (dark) volume ratio of 1:1, after the inner and outer walls have relatively rotated 40 turns (corresponding to an equivalent true strain of 1600).
Fig. 10a and b are diagrams of EBSD (back scattered electron diffraction) phase compositions and orientation diagrams (IPF) of eutectic alloys metallurgically synthesized by elemental bulk strain with a lead (bright)/tin (dark) volume ratio of 28:72 (Pb-62% Sn eutectic composition). Fig. 10c and d are EBSD (back scattered electron diffraction) phase composition diagrams and orientation diagrams (IPF) of eutectic alloys metallurgically synthesized by elemental bulk strain with a lead (bright)/tin (dark) volume ratio of 1:1 (Pb-40% Sn hypoeutectic composition).
FIG. 11 corresponds to the two strain metallurgically synthesized Pb-62% Sn alloy (filled dot data points) and Pb-40% Sn alloy (open dot data points) of FIG. 10 at room temperature at 1.0X 10-3s-1Initial strain rate of (a) tensile engineering stress-engineering strain curve. The inset is a photograph of the sample before stretching and the sample after stretching of both alloys.
Detailed Description
The method for the strain metallurgical synthesis of the multi-phase alloy according to the present invention will be further described with reference to the following embodiments.
Example 1
The raw materials in this example: bulk of alloy elements of lead and tin.
The strain metallurgy synthesis method of the multiphase alloy comprises the following steps:
(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 two-phase alloy to be synthesized in this example is a eutectic Pb-62% Sn two-phase alloy, the volume ratio of the two alloy elements lead/tin is 28: 72;
(2) preparing a circular tube-shaped combined blank (a workpiece for carrying out t-HPS processing) combined by each element block according to the volume ratio of each alloy element;
as shown in fig. 2-7, the workpieces herein may have two combinations:
the method comprises the following steps of (1) splicing a circular tube, prefabricating each alloy element block into a straight strip with a section in the shape of an arc section, wherein the ratio of central angles of the arc sections corresponding to each alloy element is equal to the designed volume ratio of the alloy, and the sum of the central angles of the arc sections corresponding to all the alloy elements is equal to 2 pi (the arc sections corresponding to all the alloy elements are spliced together to just form a spliced circular tube);
the alloy element blocks are prefabricated into element round pipes with uniform height, the diameter and the wall thickness are determined by calculating the corresponding volume ratio of the element in the alloy, and the inner diameter and the outer diameter of each round pipe can be mutually nested into a combined concentric round pipe;
all the preformed arc sections or element round pipes of the alloy elements are subjected to careful polishing and surface cleaning treatment before the assembly structure, so that pollutants and oxide layers are removed. In the splicing and combining process, the seam and the binding surface need to be in close contact without a gap;
in the embodiment, a spliced circular tube of two alloy element circular arc sections is used as a blank, the central angles of the lead/tin circular arc sections corresponding to the lead/tin circular arc sections are 101 degrees/259 degrees, and the wall thickness of the spliced circular tube is 2mm and the height of the spliced circular tube is 15 mm;
(3) respectively constraining the inner wall cylindrical surface and the outer wall cylindrical surface of the spliced circular tube blank by adopting a mandrel 1 and a ring sleeve 5, and applying axial loads to two annular end surfaces of the circular tube-shaped combined blank by using pressure rings (comprising an upper pressure ring 4 and a lower pressure ring 2), thereby realizing the full constraint of the circular tube-shaped combined blank;
under the combined action of the axial pressure of the pressure rings 2 and 4 and the constraint of the mandrel 1 and the ring sleeve 5, hydrostatic pressure of 1.2GPa is generated inside the circular tubular combined blank; meanwhile, the circular tube-shaped combined blank is subjected to primary (compression) plastic deformation, so that gaps among all element blocks are closed to achieve the effect close to cold welding, and ambient gas such as air is inhibited from entering the combined blank through the combined/spliced gaps;
(4) according to the characteristic that the plastic deformation capacity of each alloy element changes along with the temperature, a system consisting of the circular tube-shaped combined blank, the mandrel 1 for restraining the inner and outer cylindrical surfaces, the ring sleeve 5, the pressure ring for restraining the end part and the like is kept at 0.58TmIn a constant temperature environment (T)mThe melting point of tin with low melting point of lead and tin is 505.06K).
(5) At constant temperature of 0.58Tm(TmTin melting point) and the hydrostatic pressure of 1.2GPa, the fixed core shaft 1 rotates the ring sleeve 5 to perform circumferential high-pressure shearing, the plastic deformation reaches the equivalent true strain of 2000, and the designed Pb-62% Sn eutectic composition biphase alloy is synthesized. In the resultant two-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. + -. 0.1. mu.m, as shown in FIG. 10 b. The Pb-62% Sn alloy is 1.0X 10 at room temperature-3s-1Initial strain rate tensile engineering stress-engineering strain curves as shown by the solid circle data points in fig. 11, tensile elongation reaches 670%. This elongation is about equal to the highest elongation of 600% obtained in Pb-62% Sn eutectic alloys based on melting casting followed by plastic working [ T.K.Ha, Y.W.Chang, Effects of temperature and microstructure on the property in microstructure Pb-Sn alloys, Mater.Sci.Forum 357-359(2001) 159-164-]。
The inset in fig. 11 shows photographs of the corresponding alloy before and after stretching.
In the embodiment, the elongation of the eutectic Pb-62% Sn bulk superplastic alloy synthesized by directly carrying out t-HPS (high plasticity-stress high temperature sintering) large plastic deformation on bulk lead and tin is not lower than the highest elongation of a sample prepared by carrying out fusion casting alloying on the same components, and the observation and analysis of the microstructure of the sample show that the eutectic Pb-62% Sn bulk superplastic alloy achieves a high metallurgical quality level.
The parameters of the target alloy, the volume ratio of the elements of the initial bulk alloy, the constant temperature during processing, the constant pressure hydrostatic pressure, the equivalent strain of the circumferential high pressure shear, and the like in examples 2 to 4 are shown in table 1, and the other process operations are the same as those in example 1.
TABLE 1
Example 2
In this embodiment, the constant temperature is 0.58Tm(TmIs the melting point of tin) under the condition of constant pressure of 1.2GPa, the circumferential high-pressure shearing is carried out, and the plastic deformation reaches the 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. + -. 0.1. mu.m, as shown in FIG. 10 d. The Pb-40% Sn alloy is at room temperature at 1.0X 10-3s-1Initial strain rate tensile engineering stress-engineering strain curves as shown by the open circle data points in fig. 11, tensile elongation reaches 1870%. This elongation is based on the highest elongation obtained in melting cast and then working treated Pb-Sn alloys600% more than three times T.K.Ha, Y.W.Chang, Effects of temperature and microstructure on the property in microduct Pb-Sn alloys, Mater.Sci.Forum 357-359(2001)159-164]。
The inset in fig. 11 shows photographs of the corresponding alloy before and after stretching. Therefore, the technical route of synthesizing the multiphase alloy by the alloy element solid block through strain metallurgy is reflected, the limitation of the alloy uniformity caused by the precipitation of the eutectic phase in the technical route of alloy smelting and solidification shown in figure 1 is broken through, the component design of the alloy has higher freedom degree, 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 more uniformly, but there was still a sign of preferential distribution in the circumferential direction (lateral direction in fig. 8), as shown in fig. 8. The average grain size of the two phases reaches 2.1 + -0.3 μm.
Example 4
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 uniformly distributed, and no indication of preferential distribution in the circumferential direction (lateral direction in fig. 9) was recognized, as shown in fig. 9. The average grain size of the two phases reached 1.9. + -. 0.3. mu.m.
The bulk lead and tin as alloy elements and their synthesized lead-tin alloy used in the embodiments of the present invention are only examples of suitable materials, and the synthesis method of the present invention is also applicable to other materials, such as bulk aluminum, copper, nickel, niobium, iron, magnesium, indium, lithium, etc., and is synthesized into a two-phase or multi-phase alloy. The invention figures 2-5 show the schematic diagrams of the combination mode of two blanks of the split round tube and the concentric round tube, and only schematically illustrate the form of the combined blank. The kinds of alloying elements used in the synthesis of the multi-phase alloy in practice are not limited to 2, 3, 5 given in these schematic drawings, but 2 or more according to the design requirements of the alloy.
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 attributes 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, and any reference signs in the claims are not intended to be construed as limiting the claim concerned.
Furthermore, it should be understood that although the present description refers to embodiments, not every embodiment contains only one independent claim, and such description is for clarity only, and those skilled in the art will be able to make the description as a whole, and the embodiments may be appropriately combined to form other embodiments understood by those skilled in the art.
Claims (7)
1. A strain metallurgy method for synthesizing a multi-phase alloy, characterized by: the method comprises the following steps:
1) designing components according to the performance requirements and the structure requirements of the alloy, and calculating and determining the volume ratio of corresponding alloy elements according to the proportion of each alloy phase;
2) preparing a circular tube-shaped combined blank combined by blocks of the alloy elements according to the volume ratio of the alloy elements;
3) respectively constraining the inner wall cylindrical surface and the outer wall cylindrical surface of the circular tube-shaped combined blank by adopting a mandrel and a ring sleeve, and applying axial load to two annular end surfaces of the circular tube-shaped combined blank by using a pressure ring, so that hydrostatic pressure of 1 GPa-30 GPa is generated in the circular tube-shaped combined blank, and the circular tube-shaped combined blank generates preliminary plastic deformation;
4) placing the system subjected to the preliminary plastic deformation in the step 3) at the temperature of 0.20-0.90 DEGT mOr only keeping the circular tube-shaped combined blank at the constant temperature; simultaneously applying a drive torque to at least one of the mandrel and the collar to cause circumferential shear deformation thereofAnd the equivalent true strain reaches more than 1500.
2. A strain metallurgy method for synthesizing a multiphase alloy according to claim 1, characterized in that: the combination form of the circular tube-shaped combined blank comprises a spliced circular tube and a concentric circular tube,
the spliced circular tube is formed by splicing straight strips of which the cross sections are arc sections and are prefabricated from alloy element blocks, the ratio of the central angles of the 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 arc sections corresponding to all the alloy elements is equal to 2 pi;
the concentric circular tubes are composed of a plurality of circular tubes, the inner diameter and the outer diameter of which can be mutually nested into a combined concentric tube, and each circular tube is an element circular tube which is prefabricated into each alloy element block body with uniform height but the diameter and the wall thickness of which are determined by calculating the corresponding volume ratio of the element in the alloy.
3. A strain metallurgy method for synthesizing a multiphase alloy according to claim 1, characterized in that: the arc sections or the element round pipes prefabricated and formed by the alloy element blocks are subjected to surface treatment for removing pollutants and oxide layers before splicing organization, and seams are in close contact with binding surfaces in the splicing and combining process.
4. A strain metallurgy method for synthesizing a multiphase alloy according to claim 1, characterized in that: the size of each alloy element block in three dimensions is not less than 1 mm.
5. A strain metallurgy method for synthesizing a multiphase alloy according to claim 1, characterized in that: and 4) applying torque in the step 4) to provide the torque in the circumferential direction for the mandrel, and fixing the ring sleeve.
6. A strain metallurgy method for synthesizing a multiphase alloy according to claim 1, characterized in that: and in the step 4), torque is applied to fix the mandrel so as to provide circumferential torque for the ring sleeve.
7. A strain metallurgy method for synthesizing a multiphase alloy according to claim 1, characterized in that: and 4) applying torque in the step 4) to provide torque in opposite directions for the mandrel and the ring sleeve simultaneously, so that the mandrel and the ring sleeve rotate relatively around the central axis of the circular tubular blank.
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