CN117248130A - Preparation method of quick strain hardening double-yield metastable beta titanium alloy - Google Patents
Preparation method of quick strain hardening double-yield metastable beta titanium alloy Download PDFInfo
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- CN117248130A CN117248130A CN202311242459.8A CN202311242459A CN117248130A CN 117248130 A CN117248130 A CN 117248130A CN 202311242459 A CN202311242459 A CN 202311242459A CN 117248130 A CN117248130 A CN 117248130A
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- 239000000956 alloy Substances 0.000 title claims abstract description 67
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 61
- 238000005482 strain hardening Methods 0.000 title claims abstract description 34
- 229910001040 Beta-titanium Inorganic materials 0.000 title claims abstract description 25
- 238000002360 preparation method Methods 0.000 title claims abstract description 9
- 238000000034 method Methods 0.000 claims abstract description 17
- 239000010936 titanium Substances 0.000 claims abstract description 11
- 239000006104 solid solution Substances 0.000 claims description 11
- 239000012535 impurity Substances 0.000 claims description 10
- 238000010438 heat treatment Methods 0.000 claims description 9
- 238000010791 quenching Methods 0.000 claims description 6
- 230000000171 quenching effect Effects 0.000 claims description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 6
- 229910000838 Al alloy Inorganic materials 0.000 claims description 5
- 238000005098 hot rolling Methods 0.000 claims description 5
- 238000000265 homogenisation Methods 0.000 claims description 3
- 230000009467 reduction Effects 0.000 claims description 3
- 229910000734 martensite Inorganic materials 0.000 abstract description 19
- 230000000694 effects Effects 0.000 abstract description 13
- 239000013078 crystal Substances 0.000 abstract description 8
- 230000004913 activation Effects 0.000 abstract description 7
- 230000007246 mechanism Effects 0.000 abstract description 6
- 230000009466 transformation Effects 0.000 abstract description 6
- 230000008569 process Effects 0.000 abstract description 3
- 230000008859 change Effects 0.000 abstract description 2
- 238000004519 manufacturing process Methods 0.000 abstract description 2
- 229910052751 metal Inorganic materials 0.000 abstract description 2
- 239000002184 metal Substances 0.000 abstract description 2
- 229910052719 titanium Inorganic materials 0.000 abstract description 2
- 238000002844 melting Methods 0.000 description 7
- 230000008018 melting Effects 0.000 description 7
- 238000012360 testing method Methods 0.000 description 7
- 230000006698 induction Effects 0.000 description 6
- 238000003723 Smelting Methods 0.000 description 5
- 238000012512 characterization method Methods 0.000 description 5
- 238000002474 experimental method Methods 0.000 description 5
- 229910052742 iron Inorganic materials 0.000 description 5
- 239000011159 matrix material Substances 0.000 description 5
- 229910052758 niobium Inorganic materials 0.000 description 5
- 239000002245 particle Substances 0.000 description 5
- 229910001069 Ti alloy Inorganic materials 0.000 description 4
- 238000000137 annealing Methods 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- OKKJLVBELUTLKV-UHFFFAOYSA-N Methanol Chemical compound OC OKKJLVBELUTLKV-UHFFFAOYSA-N 0.000 description 3
- 230000009977 dual effect Effects 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- LRHPLDYGYMQRHN-UHFFFAOYSA-N N-Butanol Chemical compound CCCCO LRHPLDYGYMQRHN-UHFFFAOYSA-N 0.000 description 2
- 230000003213 activating effect Effects 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- VLTRZXGMWDSKGL-UHFFFAOYSA-N perchloric acid Chemical compound OCl(=O)(=O)=O VLTRZXGMWDSKGL-UHFFFAOYSA-N 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000007921 spray Substances 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000005868 electrolysis reaction Methods 0.000 description 1
- 238000001887 electron backscatter diffraction Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000000877 morphologic effect Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 238000004321 preservation Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 230000002459 sustained effect Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
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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
- C22C1/02—Making non-ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
The invention relates to a preparation method of a quick strain hardening double-yield metastable beta titanium alloy, belonging to the field of metal manufacturing. The invention aims to solve the problem of a low yield platform on the premise of introducing phase change induced plasticity and twin crystal induced plasticity effects to obtain remarkable work hardening capacity, thereby obtaining good comprehensive mechanical properties. The alloy consists of Ti, nb, fe and Al elements, wherein the conventional phase transformation product stress induced alpha ' martensite in the deformation process is replaced by the stress induced alpha ' martensite with high activation stress, and the mechanism of deformation induced {332} twin crystal, alpha ' martensite twin crystal, deformation induced omega phase transformation and the like are activated sequentially, so that the strain hardening rate is promoted to develop to a higher level rapidly. The first yield strength at room temperature can reach 573MPa, the uniform elongation can reach 16%, and the strain hardening rate is close to 4GPa.
Description
Technical Field
The invention relates to a preparation method of a quick strain hardening double-yield metastable beta titanium alloy, belonging to the field of metal manufacturing.
Background
In recent years, titanium alloys have been widely used in the field of aviation industry and the like because of their high specific strength and good corrosion resistance. However, most conventional high strength titanium alloys exhibit the disadvantage of poor ductility, with uniform elongation typically less than 10%. In order to expand the application range of the titanium alloy, a novel metastable beta titanium alloy is designed and developed by introducing a transformation induced plasticity (TRIP) effect and a twin induced plasticity (TWIP) effect. Metastable beta titanium alloys exhibit a phase-stable, sensitive deformation mode, and strength-plastic bonding is achieved by adjusting the beta phase stable alloys to exhibit excellent ductility. The excellent mechanical properties of the high strength, high ductility TRIP/TWIP titanium alloys of Ti-12Mo and Ti-9Mo-6W and the like developed at present are derived from the {332} <113> and {112} <111> mechanical twins of stress induced Body Centered Cubic (BCC) beta to orthogonal alpha "martensitic transformation and/or beta matrix. Due to the diversity of deformation mechanisms, alloys exhibit relatively high peak strain hardening rates (2000 MPa), whereas the pseudo-elasticity caused by activation of the stress-induced α "martensite at the initial stage of deformation results in the alloy yield strength remaining at a low level (200-500 MPa). In order to meet the requirements of advanced structural applications, class II metastable beta titanium alloys that exhibit only twinning and dislocation slip are of great interest, and alloys such as Ti-15Mo and Ti-10Mo-1Fe have been developed. These alloys exhibit relatively high yield strength but reduced strain hardening capacity.
Alloys with dual yield effects generally exhibit excellent strain hardening capabilities. The Ti-10V-2Fe-3Al alloy is one of the most widely used metastable beta titanium alloys, which exhibits a peak strain hardening rate of up to 12000MPa after first yielding, accompanied by a sustained activation of stress-induced alpha' martensite and tends to saturate. However, the naturally low yield of α "martensite results in the appearance of a 220MPa yield plateau and does not exhibit significant strain hardening immediately after yield. Therefore, there is a need to further tailor the deformation mechanism of TRIP/TWIP alloys to achieve both high yield strength and high strain hardening rate.
Disclosure of Invention
The invention aims to solve the problem that a double-yield metastable beta titanium alloy is easy to have a low yield platform, and provides a preparation method of a quick strain hardening double-yield metastable beta titanium alloy; the method aims to solve the problem of a low yield platform on the premise of introducing phase change induced plasticity and twin crystal induced plasticity effects to obtain remarkable work hardening capacity, so that good comprehensive mechanical properties are obtained. The alloy consists of Ti, nb, fe and Al elements, wherein the conventional phase transformation product stress induced alpha ' martensite in the deformation process is replaced by the stress induced alpha ' martensite with high activation stress, and the mechanism of deformation induced {332} twin crystal, alpha ' martensite twin crystal, deformation induced omega phase transformation and the like are activated sequentially, so that the strain hardening rate is promoted to develop to a higher level rapidly.
The aim of the invention is achieved by the following technical scheme.
A preparation method of a quick strain hardening double yield metastable beta titanium alloy,
the invention provides a double-yield metastable beta titanium alloy material without a low yield platform, which comprises the steps of carrying out homogenization heat treatment and subsequent hot rolling on Ti-Nb-Fe-Al alloy; heating the Ti-Nb-Fe-Al alloy material to a solid solution temperature T1 and preserving heat for a period of time T1, and then directly performing water quenching within 1min at intervals to obtain the double-yield metastable beta titanium alloy; t1=880-920 ℃, t1=50-60 min.
By activating the high activation stress induced alpha' martensite during the yield phase, rather than activating the low activation stress induced alpha "martensite common in dual yield metastable beta titanium alloys, the alloy achieves higher yield strength and rapid strain hardening occurs, avoiding the occurrence of low yield platforms.
Preferably, the metastable beta titanium alloy material is prepared by vacuum melting.
Preferably, the homogenization temperature is 1000 ℃, and the heat preservation time is 10 hours; the hot rolling temperature was 720℃and the total reduction was 75%.
Preferably, the water quenching temperature is 15-30 ℃.
Preferably, the addition amounts are 15-17wt.% of Nb, 1-2wt.% of Fe, 0-2wt.% of Al, the balance being commercially pure Ti and unavoidable impurities, the impurity content being less than 0.02%.
The beneficial effects are that:
(1) The metastable beta titanium alloy material disclosed by the invention has the composition of Ti-17Nb-2Fe-2Al (wt%), so that on one hand, the low yield platform of the alloy after first yielding is avoided, and the first yielding occurs at the strength of 573 MPa; on the other hand, the activation of the complex deformation mechanism in the yield stage effectively improves the strain hardening rate of the alloy, and the strain hardening rate higher than 2GPa and the peak strain hardening rate of 4GPa are always kept in the strain range of 7.8%.
(2) Compared with the reported metastable beta titanium alloy, the preparation method of the double-yield metastable beta titanium alloy without the low yield platform disclosed by the invention can provide a thought for the existing alloy design method and provide a reference for the deformation mechanism research of the Ti-Nb-based metastable beta titanium alloy.
Additional advantages, objects, and features of the invention will be set forth in part in the description which follows and in part will become apparent to those having ordinary skill in the art upon examination of the following or may be learned from practice of the invention. The objects and other advantages of the invention may be realized and obtained by means of the instrumentalities and combinations particularly pointed out in the specification.
Drawings
FIG. 1 is a graph of engineering stress-strain for a solid solution Ti-17Nb-2Fe-2Al alloy at room temperature;
FIG. 2 is a graph of true stress-strain curve and strain hardening rate for a solid solution Ti-17Nb-2Fe-2Al alloy at room temperature;
FIG. 3 is a microstructure of a solid solution Ti-17Nb-2Fe-2Al alloy. Wherein, the graph a is a low-power EBSD BC graph, and the graph b is a dark-field image graph of omega phase in the matrix;
FIG. 4 is a microstructure of a solid solution Ti-17Nb-2Fe-2Al alloy at a deformation of 1.5%. Wherein, figure a is a stress-induced alpha' martensite dark field image graph generated by deformation, and figure b is a {332} twin crystal dark field image graph generated by deformation;
FIG. 5 is a microstructure of a solid solution Ti-17Nb-2Fe-2Al alloy at a deformation of 3%. Wherein, figure a is a stress-induced alpha' martensite bright field image generated by deformation, and figure b is a dark field image of the same region;
FIG. 6 is a microstructure of a solid solution Ti-17Nb-2Fe-2Al alloy at a deformation of 5%. Wherein figure a is a plot of stress induced α' martensite and {332} twin IPF produced by deformation and figure b is a plot of stress induced ω lath dark field produced by deformation.
Detailed description of the preferred embodiments
The invention will now be described in detail with reference to specific examples which will assist the person skilled in the art in further understanding the invention, but which are not intended to limit the invention in any way. It should be noted that several modifications can be made without departing from the inventive concept, which fall within the scope of the present invention.
Example 1
The embodiment is a preparation method of a rapid strain hardening double-yield metastable beta titanium alloy material, wherein the main constituent elements and mass percentages of the alloy are as follows: 17% of Nb,2% of Fe,2% of Al, the balance of Ti and other unavoidable impurity elements, and adopting a vacuum induction melting furnace to prepare an ingot, wherein the method comprises the following steps of:
s1, taking pure Ti particles with the purity of 99.99 percent, pure Nb particles with the purity of 99.95 percent, pure Fe particles with the purity of 99.99 percent and pure Al particles with the purity of 99.99 percent as raw materials, mixing according to the mass percent, smelting in a vacuum arc smelting furnace, and adopting high-purity argon as a protective atmosphere.
S2, turning over the cast ingot obtained by the smelting in the previous step, and smelting again by adopting the same parameters, wherein the smelting is repeated for 3 times.
S3, placing the finished cast ingot in a vacuum degree lower than 3X10 -4 Vacuum homogenizing annealing treatment is carried out in a heat treatment furnace of Pa, the temperature is firstly increased to 1000 ℃ along with the furnace, the annealing treatment is carried out at the temperature for 10 hours, and then the annealing treatment is cooled to the room temperature along with the furnace.
S4, casting the ingot after the vacuum homogenizing annealing treatment at the vacuum degree of less than 3 multiplied by 10 -4 Heating to 720 ℃ in a Pa vacuum environment, preserving heat and heating thoroughly, immediately adopting a double rolling mill to carry out multi-pass hot rolling, keeping the rolling reduction of each pass at not more than 0.5mm, returning to a furnace for preserving heat for 1min between passes, keeping the total deformation at 75%, and then carrying out water cooling.
S5, the plate after cold rolling treatment is subjected to vacuum degree of less than 5 multiplied by 10 -3 And (3) carrying out solution treatment in a heat treatment furnace of Pa, after the furnace temperature is raised to 900 ℃ and is stable, putting a sample, preserving the heat at the temperature for 60min, and then carrying out water cooling quenching.
S6, respectively carrying out room-temperature quasi-static tensile detection on the solid solution samples, carrying out TEM microstructure characterization on the solid solution samples with deformation amounts of 1.5%, 3% and 5%, and observing through Thermo Fisher Talos F X200. The transmission sample is prepared by using a Struers Tenupol-5 electrolysis double spray instrument, wherein double spray liquid is 60% methanol+30% n-butanol+10% perchloric acid, the temperature is-25 ℃ to-30 ℃, and the voltage is 15-20V.
Experimental results:
1. and (5) testing mechanical properties.
According to GB/T228.1-2010 section 1 of tensile test of metallic materials: the room temperature test method measures the mechanical properties of the alloy prepared in the embodiment 1, the engineering stress-engineering strain curve is shown in figure 1, and the result shows that the yield strength is 573MPa, and the alloy has relatively good elongation after break of 15.6%. The strain hardening rate curve is shown in fig. 2, and the result shows that a higher strain hardening rate value is maintained after yielding, and the strain hardening rate peak value is 4GPa in the subsequent deformation process.
2. Microstructure characterization.
The microstructure of the solid solution state alloy matrix is shown in figure 3a, and the result shows that the matrix is completely composed of single-phase equiaxed beta grains, and alpha phase does not appear; as shown in fig. 3b, nano omega-phase particles occurring during quenching are dispersed in the beta grains of the matrix. Characterization of the structure after 1.5% quasi-static deformation showed that the stress-induced α' martensitic phase began to appear in the β grains as shown in fig. 4a, while {332} twin crystals could also be found to begin to form by virtue of the stress-induced α "martensitic phase as a transitional phase as shown in fig. 4 b. Characterization of the 3% quasistatic deformed tissue shows that the number of stress-induced alpha 'martensite phases is gradually increased as shown in the bright field image of fig. 5a, and the morphological characteristics of the stress-induced alpha' martensite are more clearly shown in the dark field image of fig. 5 b. Characterization of the tissue at 5% deformation showed massive occurrence of {332} twinning as shown in FIG. 6a and the generation of stress-induced omega laths as shown in FIG. 6 b.
Table 1, quasi-static tensile properties test comparison of each component alloy.
Example 2
The alloy in the example comprises the following main components in percentage by mass: 17% Nb,2% Fe,2% Al,1% Ni, the balance Ti and other unavoidable impurity elements, and ingots were prepared by a vacuum induction melting furnace, the foregoing procedure being consistent with example 1.
The alloy prepared and processed in the second embodiment is subjected to quasi-static room temperature mechanical property test. Experiments show that: the alloy has a room temperature yield strength of 520MPa and a fracture strain of 42%, and the strain hardening effect is weaker resulting in a tensile strength much lower than that of example 1, while not possessing the dual yield characteristics.
Example 3
The alloy in the example comprises the following main components in percentage by mass: 17% Nb,2% Fe,2% Al,1% Zr, the balance being Ti and other unavoidable impurity elements, and ingot casting was made using a vacuum induction melting furnace, the foregoing procedure being consistent with example 1.
The alloy prepared and processed in the third embodiment is subjected to quasi-static room temperature mechanical property test. Experiments show that: the alloy has double yield effect and obvious strain hardening effect, but the room temperature yield strength is only 350MPa, and the fracture strain is 27%.
Example 4
The alloy in the example comprises the following main components in percentage by mass: 17% Nb,2% Fe,2% Al,2% Co, the balance Ti and other unavoidable impurity elements, and ingots were prepared by a vacuum induction melting furnace, the foregoing procedure being consistent with example 1.
The alloy prepared and processed in the fourth embodiment is subjected to quasi-static room temperature mechanical property test. Experiments show that: the alloy has a room temperature yield strength of 720MPa and a breaking strain of 17%, but does not have a double yield effect or a strain hardening effect.
Comparative example 1
The alloy in the example comprises the following main components in percentage by mass: 17% Nb,2% Fe, the balance Ti and other unavoidable impurity elements, and a vacuum induction melting furnace was used to make ingots, the foregoing procedure being consistent with example 1.
The alloy prepared and processed in comparative example one was also subjected to quasi-static room temperature mechanical property testing. Experiments show that: the alloy has the room temperature yield strength of 600MPa and the breaking strain of 6 percent, does not have double yield effect and obvious strain hardening effect.
Comparative example 2
The alloy in the example comprises the following main components in percentage by mass: 17% Nb,1% Fe, the balance Ti and other unavoidable impurity elements, and a vacuum induction melting furnace was used to make ingots, the foregoing procedure being consistent with example 1.
The alloy prepared and processed in the second comparative example is subjected to quasi-static room temperature mechanical property test. Experiments show that: the alloy has the room temperature yield strength of 500MPa and the breaking strain of 12 percent and has double yield effect.
While the foregoing is directed to embodiments of the present invention, other and further embodiments of the invention may be devised without departing from the basic scope thereof, and the scope thereof is determined by the claims that follow.
Claims (4)
1. A preparation method of a quick strain hardening double yield metastable beta titanium alloy is characterized by comprising the following steps: firstly carrying out homogenization heat treatment and subsequent hot rolling on Ti-Nb-Fe-Al alloy; heating the Ti-Nb-Fe-Al alloy material to a solid solution temperature T1 and preserving heat for a period of time T1, and then directly performing water quenching within 1min at intervals to obtain the double-yield metastable beta titanium alloy; t1=880-920 ℃, t1=50-60 min.
2. The method for preparing the rapid strain hardening double yield metastable beta titanium alloy according to claim 1, wherein the method comprises the following steps: homogenizing heat treatment at 1000 deg.c for 10 hr; the hot rolling temperature was 720℃and the total reduction was 75%.
3. The method for preparing the rapid strain hardening double yield metastable beta titanium alloy according to claim 1, wherein the method comprises the following steps: the water quenching temperature is 15-30 ℃.
4. The method for preparing the rapid strain hardening double yield metastable beta titanium alloy according to claim 1, wherein the method comprises the following steps: the addition amount of the Ti-Nb-Fe-Al alloy is 17wt.% of Nb, 2wt.% of Fe and 2wt.% of Al, and the balance is commercially pure Ti and unavoidable impurities, wherein the impurity content is less than 0.02%.
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