CN104726730A - Method for preparing laminated-structured Ti-(TiB+La2O3)/Ti composite material - Google Patents
Method for preparing laminated-structured Ti-(TiB+La2O3)/Ti composite material Download PDFInfo
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Abstract
The invention provides a method for preparing a laminated-structured Ti-(TiB+La2O3)/Ti composite material. The method comprises the following steps of calculating the mass of Ti powder and LaB6 powder needed for preparing reinforcement material according to the volume fraction of the reinforcement material, and weighing the Ti powder and the LaB6 powder; ball-milling the Ti powder and the LaB6 powder, and mixing uniformly to obtain mixed powder; taking Ti powder additionally, laying the Ti powder and the mixed powder in a mould alternately in layers, and performing cold pressing and forming to obtain a laminated-structured prefabricate; performing high-temperature densification sintering on the laminated-structured prefabricate in vacuum, furnace-cooling and taking the prefabricate out to obtain the laminated-structured Ti-(TiB+La2O3)/Ti composite material. The relative density of the laminated-structured Ti-(TiB+La2O3)/Ti composite material is further improved by adopting multi-channel high-temperature hot rolling, grains are refined, the distribution of the reinforcement material is improved, and layer thickness is obviously reduced.
Description
Technical field
The present invention relates to the preparation method of layered titanium based composites, be specifically related to a kind of powder metallurgy that adopts and prepare stratiform structure Ti-(TiB+La
2o
3the method of)/Ti matrix material.
Background technology
Titanium or titanium alloy density is little, specific tenacity is high, corrosion-and high-temp-resistant is good, is widely used in the fields such as aerospace, boats and ships, medical treatment, sports apparatus, the chemical industry energy.When titanium alloy material develops into the limit close to certain performance, the simple change solid solution element that relies on just is difficult to the raising having matter in performance, now can select by adding reinforcement to obtain higher performance in alloy.Since the seventies in last century, carry out numerous research about titanium matrix composite both at home and abroad one after another, be mainly divided into continuous fiber reinforcing titanium matrix composite and particulate reinforced composite according to reinforcement kind difference.Wherein fiber reinforced titanium matrix composite limits its investigation and application due to the restriction of the factors such as complex process, high cost, surface reaction.Granule intensified titanium-base compound material is divided into again additional reinforcement particle and reaction in－situ to generate two kinds, and wherein in-situ reactive synthesis method can avoid introducing pollution and surface reaction to ensure the good combination of matrix and reinforcement simultaneously.Current in-situ reactive synthesis method mainly contains: self-propagating high-temperature synthesis method, heat release diffusion process, fusion casting, rapid solidification method and powder metallurgic method.Research shows the introducing of fabricated in situ reinforcement, is conducive to the mechanical property such as intensity, modulus, wear resistance improving matrix material.But along with the increase of reinforcement content in Titanium base, although titanium matrix composite strength and stiffness significantly improve, but can cause the significantly reduction of toughness and damage tolerance, until present overall fragility and make application be restricted, this also becomes the Main Bottleneck of restriction titanium matrix composite application simultaneously.
Make a general survey of occurring in nature, through the natural selection such as natural selection, the survival of the fittest, the material of multiple bioselection oneself existence the most applicable builds the health of oneself, and as bamboo, shell etc., these natural biologic materials often to have excellent performance.Deepen continuously along with to the research of biomaterial, people start to recognize that this preparation of biomaterial to modern material with excellent properties has reference and evocation, so create the new research field of Materials science gradually---biomimetic material.Wherein, the nacreous layer in shell biology receives much concern because having outstanding mechanical property.The lamellar structure meticulous by shell in the Nature inspires, Clegg has carried out structure Bionic Design, first the lamellar ceramic composite that this lamellar structure has prepared high tenacity, major rupture merit is simulated, after achievement is delivered on Nature, become rapidly one of study hotspot of nearly 10 years stupaliths.The research such as the Liuyi Xiang of Northwestern Polytechnical University finds that in HfC-SiC pottery, introduce more weak BN layer can significantly improve fracture toughness property, and reason comprises the multiple toughening mechanisms such as crack branching, deflection, layering.The Lin Jiang of Shanghai Communications University etc. adopt a kind of flake powder metallurgical method to prepare Al
2o
3/ Al and CNTs/Al stratified composite, research finds that the laminate structure of high-sequential can hold more dislocation and CNTs, obtains high intensity and toughness.The B.X.Liu of Harbin Institute of Technology etc. adopt reaction hot-pressing and diffusion welding to prepare TiBw/Ti stratified composite, and research finds that pure titanium layer and the composite layer Layered titanium matrix composite that acts synergistically can obtain higher plasticity and toughness.
The conventional preparation technology of current layered titanium based composites has: the multiple methods such as Rolling compund, hot pressed sintering, diffusion welding, thermospray, surface overlaying, electrochemical deposition and consumable arc-melting method.But being difficult in preparation process to avoid introduces defect in interface, Coating combination is more weak, and when causing stratified material stand under load, crackle is easy to expand rapidly along interface layer finally cause comprehensive mechanical property poor, is difficult to the highly malleablized effect effectively realizing laminate structure.The present invention uses for reference occurring in nature concba lamellar structure and carries out configured, and adopt powder metallurgy and high-temperature hot rolling for layered titanium based composites, the matched well of obdurability is realized by the synergy of high-strength compound layer and the pure titanium layer of high-ductility, reach the object improving traditional discontinuous granule intensified titanium-base compound material toughness, obtain the layered titanium based composites possessing excellent comprehensive performance.
Summary of the invention
The present invention solves the technical problem that existing discontinuous granule intensified titanium-base compound material toughness is poor and layered titanium based composites Coating combination is more weak, and provides a kind of powder metallurgy that adopts to prepare stratiform structure Ti-(TiB+La
2o
3the method of)/Ti matrix material.
For achieving the above object, the invention provides one and prepare stratiform structure Ti-(TiB+La
2o
3the method of)/Ti matrix material, the method comprises the steps:
Ti powder needed for preparation reinforcement and LaB is converted out according to the volume fraction of reinforcement
6the quality of powder, and take Ti powder and LaB
6powder, specifically according to the reaction in－situ formula 12Ti+2LaB under both high temperature
6+ 3 [O]=12TiB+La
2o
3calculate Ti powder and LaB when final reinforcement volume fraction is respectively 5%, 10%, 15%
6the ratio of powder, takes required Ti powder and LaB according to calculation result
6powder;
By described Ti powder and LaB
6after ball milling is carried out in powder mixing, adopt rotating speed to be 150r/min gyratory shaker mixing 15min, obtain mixed powder;
Separately get Ti powder, after alternative stacked is laid in a mold by described titanium valve and mixed powder, under the pressure of 50 ~ 100T, carry out coldmoulding 1 ~ 3min, obtain laminate structure precast body;
By layered structure precast body 10
-3under the vacuum tightness of Pa, be at the uniform velocity warming up to 1200 ~ 1300 DEG C with the speed of 10 ~ 20 DEG C/min, after insulation 1 ~ 4h, furnace cooling takes out, and obtains laminate structure Ti-(TiB+La
2o
3)/Ti matrix material.
Preferably, the method also comprises the steps: layered titanium matrix composite to carry out multistage hot deformation at 1000 ~ 1100 DEG C.
Preferably, described Ti powder and LaB
6the particle diameter of powder is respectively 100 μm and 50 μm.
Preferably, the condition of described ball milling is: take agate ball as abrading-ball, and ratio of grinding media to material is (1 ~ 5): 1.
Preferably, described reinforcement is at Ti-(TiB+La
2o
3volume fraction in)/Ti matrix material is 5%, 10% or 15%.
Compared with prior art, the invention has the advantages that:
The present invention utilizes Ti and LaB
6reaction in－situ under 1300 DEG C of high temperature obtains the (TiB+La in layered titanium based composites
2o
3)/Ti matrix material strengthening layer, i.e. reinforcement, utilizes the densification sintering of Ti powder under 1300 DEG C of high temperature simultaneously, obtains the layered titanium based composites with higher-density, and LaB
6reaction in－situ can oxygen uptake, the oxygen level of stratiform titanium matrix composite can be reduced, further improving SNR.
The present invention adopts the hot rolling of multi-pass high temperature to improve laminate structure Ti-(TiB+La further
2o
3the relative density of)/Ti matrix material, crystal grain thinning also improves reinforcement distribution, significantly reduces thickness simultaneously, improves over-all properties further by dimensional effect.
(the TiB+La of layered titanium based composites of the present invention
2o
3)/Ti composite layer, Ti layer and interface zone original state are all powder, under identical conditions, sinter rear three regions can possess consistent relative density, so layered titanium based composite material interface region prepared by the present invention is no longer in conjunction with bad defect area, but (TiB+La
2o
3even transition layer between)/Ti composite layer and Ti layer.
The present invention can by adjustment (TiB+La
2o
3)/Ti composite layer reinforcement content, (TiB+La
2o
3)/Ti composite layer thickness, pure titanium layer thickness and both Thickness ratio, adjust the highly malleablized effect of stratiform titanium matrix composite, obtains the stratified material with different mechanical properties.
Laminate structure Ti-(TiB+La prepared by the present invention
2o
3)/Ti matrix material compared to simple pure titanium material and granule intensified titanium-base compound material, (TiB+La
2o
3in)/Ti layer, the existence of reinforcement can obvious crystal grain thinning, simultaneously high-load can be born and to crack deflection, postpone the constriction of pure titanium layer, improve uniform plastic deformation ability, and a large amount of viscous deformation of pure titanium layer can improve the brittle fracture mode of matrix material by passivation crackle, make its general performance go out good highly malleablized effect.
Accompanying drawing explanation
By reading the detailed description done non-limiting example with reference to the following drawings, other features, objects and advantages of the present invention will become more obvious:
Fig. 1 is stratiform Ti-(TiB+La prepared by test 1
2o
3)/Ti matrix material; Wherein 1a is cross section macroscopic body formula microphotograph, and 1b is Ti layer, and 1c is (TiB+La
2o
3)/Ti composite layer, 1d is interface zone, and 1e is shape of reinforcing phase under high power;
Fig. 2 is the (TiB+La of reinforcement volume fraction 5% prepared by test 1
2o
3)/Ti matrix material control sample photo; Wherein 2a is Stereo microscope photo, and 2b is stereoscan photograph.
Embodiment
Below in conjunction with specific embodiment, the present invention is described in detail.Following examples will contribute to those skilled in the art and understand the present invention further, but not limit the present invention in any form.It should be pointed out that to those skilled in the art, without departing from the inventive concept of the premise, some distortion and improvement can also be made.These all belong to protection scope of the present invention.
embodiment 1
Step one, take raw material Ti powder and LaB
6powder: Ti powder footpath used is about 100 μm, LaB
6powder footpath is about 50 μm.According to the reaction in－situ formula 12Ti+2LaB under both high temperature
6+ 3 [O]=12TiB+La
2o
3calculate Ti powder and LaB when final reinforcement volume fraction is respectively 5%, 10%, 15%
6the ratio of powder, Ti powder massfraction 93.4% ~ 97.8%, LaB
6powder massfraction 2.2% ~ 6.6%, Ti powder and LaB according to the Size calculation of special die used and under taking three kinds of reinforcement volume fraction
6the quality of powder is respectively 46.78g, 1.05g; 45.78g, 2.09g; 44.78g, 3.14g;
Step 2, preparation Ti powder and LaB
6the powder mix of powder: the Ti powder that step one is taken and LaB
6powder is placed in ball grinder, and ratio of grinding media to material is 5:1, adopts rotating speed to be 150r/min gyratory shaker mixing 15min, obtains uniform powder mix;
Step 3, Ti powder and powder mix alternative stacked obtain laminate structure: the quality calculating the powder mix obtained in the Ti powder of 1mm thickness and step 2 according to die size respectively, take and the alternative stacked laying in special mould by powder mix and Ti powder, obtain the laminate structure amounting to 20 shelf theory thickness 1mm;
Step 4, cold-press moulding obtain layered titanium based composites precast body: the powder of alternative stacked in step 3 is placed in cold-press moulding under YA32-315 four-column universal hydraulic press together with mould, keeps 1min, obtain laminate structure precast body under 60T pressure;
Step 5, vacuum sintering obtain layered titanium based composites: insert in vacuum sintering furnace by step 4 sandwich precast body, be evacuated to 10
-3pa, temperature at the uniform velocity rises to 1300 DEG C with the temperature rise rate of 10 DEG C/min, and after being incubated 1h at this temperature, furnace cooling takes out, and obtains layered titanium based composites;
Step 6, high temperature hot rolling improve layered titanium based composites weave construction: carry out the hot rolling of multi-pass high temperature, temperature 1050 DEG C, final deformation amount 70% to the layered titanium based composites after sintering in step 5.Improve stratiform Ti-(TiB+La
2o
3the density of)/Ti matrix material, crystal grain thinning, improves reinforcement distribution, and reduces pure titanium layer and (TiB+La
2o
3the thickness of)/Ti composite layer.
Step 7, preparation (TiB+La as a comparison
2o
3)/Ti matrix material: contrast sample reinforcement volume fraction is 5%, and concrete steps are: according to reaction formula 12Ti+2LaB
6+ 3 [O]=12TiB+La
2o
3calculate Ti powder and LaB when reinforcement volume fraction is respectively 5%
6the ratio of powder, takes Ti powder 93.6g, LaB
6powder 2.1g is also placed in ball grinder, is uniformly mixed 10min and obtains uniform powder mix, powder mix to be poured in special die into cold-press moulding under press and obtains (TiB+La
2o
3)/Ti composite preform, inserts precast body in vacuum sintering furnace, is evacuated to 10
-3pa, temperature at the uniform velocity rises to 1300 DEG C with the temperature rise rate of 10 DEG C/min, and after being incubated 1h at this temperature, furnace cooling takes out, and obtains (the TiB+La of reinforcement volume fraction 5%
2o
3)/Ti matrix material.
comparative example 1
This comparative example is with the difference of embodiment 1, and reinforcement material is Graphite Powder 99, and in addition, each step is identical with embodiment 1.
comparative example 2
This comparative example is with the difference of embodiment 1 or comparative example 1, and reinforcement material is B
4c powder, in addition, each step is identical with embodiment 1.
With the laminate structure Ti-(TiB+La that embodiment 1 obtains
2o
3)/Ti matrix material and particle reinforce (TiB+La
2o
3)/Ti matrix material contrast sample is example, adopts Linear cut to be cut by sample, obtains specimen cross section, after polishing, polishing and corrosion, carry out observation analysis, and concrete test is as follows:
Adopt model to be the Stereo microscope of Stemi 2000-C and model to be the stratiform Ti-(TiB+La that the field emission scanning electron microscope of FEI QUANTA 250 is prepared test one
2o
3)/Ti matrix material is observed, and obtains photo shown in accompanying drawing 1, and wherein (1a) is Stereo microscope photo, can find out Ti layer and (TiB+La in stratified material
2o
3)/Ti composite layer is fairly obvious, and wherein homogeneous dark colored portion is Ti layer, and Dispersed precipitate light-colored particles part for (TiB+La
2o
3)/Ti composite layer; (1b) be Ti layer; (1c) be interface zone; (1d) be (TiB+La
2o
3)/Ti composite layer; (1e) be (TiB+La under high power
2o
3shape of reinforcing phase in)/Ti composite layer.(TiB+La can be found out
2o
3in)/Ti composite layer, crystal whisker-shaped TiB reinforcement is uniformly distributed, and is combined well with matrix, and compared with pure titanium layer, the existence of TiB reinforcement can obvious refinement matrix grain, can significantly improve the mechanical property of matrix.Interface zone is observed simultaneously and can find pure titanium layer and (TiB+La
2o
3be even transition gradually between)/Ti composite layer, Presence of an interface is not in conjunction with bad defect, makes this region be no longer weak link in whole laminate structure.
Adopting model to be the Stereo microscope of Stemi 2000-C and model is that the field emission scanning electron microscope of FEI QUANTA 250 is to (TiB+La as a comparison
2o
3)/Ti matrix material is observed, and as shown in Figure 2, wherein 2a is Stereo microscope photo, and 2b is stereoscan photograph.As can be seen from the figure TiB reinforcement is uniformly distributed in Ti matrix, this and laminate structure Ti-(TiB+La
2o
3(TiB+La in)/Ti matrix material
2o
3)/Ti composite layer is consistent.
Above specific embodiments of the invention are described.It is to be appreciated that the present invention is not limited to above-mentioned particular implementation, those skilled in the art can make various distortion or amendment within the scope of the claims, and this does not affect flesh and blood of the present invention.
Claims (5)
1. prepare stratiform structure Ti-(TiB+La for one kind
2o
3the method of)/Ti matrix material, is characterized in that, comprise the steps:
Ti powder needed for preparation reinforcement and LaB is converted out according to the volume fraction of reinforcement
6the quality of powder, and take Ti powder and LaB
6powder;
By described Ti powder and LaB
6after ball milling is carried out in powder mixing, stirring and evenly mixing, obtains mixed powder;
Separately get Ti powder, after alternative stacked is laid in a mold by described titanium valve and mixed powder, under the pressure of 50 ~ 100T, carry out coldmoulding 1 ~ 3min, obtain laminate structure precast body;
By layered structure precast body 10
-3under the vacuum tightness of Pa, be at the uniform velocity warming up to 1200 ~ 1300 DEG C with the speed of 10 ~ 20 DEG C/min, after insulation 1 ~ 4h, furnace cooling takes out, and obtains laminate structure Ti-(TiB+La
2o
3)/Ti matrix material;
Wherein, described reinforcement is TiB and La
2o
3mixture.
2. preparation method as claimed in claim 1, is characterized in that, also comprise the steps: layered Ti-(TiB+La
2o
3)/Ti matrix material carries out multistage hot deformation at 1000 ~ 1100 DEG C.
3. preparation method as claimed in claim 1, is characterized in that, described Ti powder and LaB
6the particle diameter of powder is respectively 100 μm and 50 μm.
4. preparation method as claimed in claim 1, it is characterized in that, the condition of described ball milling is: take agate ball as abrading-ball, and ratio of grinding media to material is (1 ~ 5): 1.
5. preparation method as claimed in claim 1, it is characterized in that, described reinforcement is at Ti-(TiB+La
2o
3volume fraction in)/Ti matrix material is 5%, 10% or 15%.
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106853530A (en) * | 2017-01-13 | 2017-06-16 | 哈尔滨工业大学 | A kind of method that powdering hot pressed sintering prepares stratiform titanium matrix composite |
| CN107414086A (en) * | 2017-08-14 | 2017-12-01 | 陕西理工大学 | A kind of carbide cooperates with Strengthening and Toughening TiAl-base alloy and preparation method thereof with titanium alloy layer |
| CN108796265A (en) * | 2018-06-28 | 2018-11-13 | 北京理工大学 | A kind of preparation method of TiB nanometers of enhancing titanium matrix composite |
| CN112063875A (en) * | 2020-09-21 | 2020-12-11 | 哈尔滨工业大学 | Method for preparing shell-like laminated structure Ti2 AlNb-based composite material by combining powder metallurgy and forging |
| CN112662904A (en) * | 2020-11-23 | 2021-04-16 | 北京理工大学 | TiB and La2O3Preparation method of reinforced titanium-based composite material |
| CN112775437A (en) * | 2020-12-23 | 2021-05-11 | 西南交通大学 | Light metal-based composite material part and preparation method thereof |
| CN114131015A (en) * | 2021-12-13 | 2022-03-04 | 上海交通大学 | Confined powder filling method for preparing configuration composite material |
| CN114888289A (en) * | 2022-05-10 | 2022-08-12 | 哈尔滨工业大学 | Gradient titanium-based composite material and preparation method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101074464A (en) * | 2007-06-21 | 2007-11-21 | 上海交通大学 | Composite heat-resisting enhance titanium alloy |
| CN102672187A (en) * | 2012-05-08 | 2012-09-19 | 哈尔滨工业大学 | Preparation methods of layered titanium matrix composite material |
| CN104263984A (en) * | 2014-10-14 | 2015-01-07 | 哈尔滨工业大学（威海） | Preparation method of TiBw/Ti-6Al-4V composite bar adopting quasi-continuous reticular structure |
-
2015
- 2015-02-09 CN CN201510067811.8A patent/CN104726730B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101074464A (en) * | 2007-06-21 | 2007-11-21 | 上海交通大学 | Composite heat-resisting enhance titanium alloy |
| CN102672187A (en) * | 2012-05-08 | 2012-09-19 | 哈尔滨工业大学 | Preparation methods of layered titanium matrix composite material |
| CN104263984A (en) * | 2014-10-14 | 2015-01-07 | 哈尔滨工业大学（威海） | Preparation method of TiBw/Ti-6Al-4V composite bar adopting quasi-continuous reticular structure |
Non-Patent Citations (7)
| Title |
|---|
| XIANG-LONG GUO等: "Microstructure and mechanical properties of (TiB+La2O3)/Ti composites heat treated at different temperatures", 《TRANS.NONFERROUS MET.SOC.CHINA》 * |
| 周鹏等: "粉末冶金制备原位自生钛基复合材料的显微组织和力学性能研究", 《粉末冶金工业》 * |
| 孙康宁等: "《碳纳米管复合材料》", 31 January 2010, 机械工业出版社 * |
| 孙洪强: "微合金化与原位颗粒协同作用铝基复合材料的组织与性能", 《江苏大学2007年度硕士学位论文》 * |
| 李云钢: "原位自生钛基复合材料高温持久性能研究", 《上海交通大学2008年度硕士学位论文》 * |
| 郭相龙等: "热轧钛基复合材料的微观组织和力学性能", 《中国有色金属学报》 * |
| 金培鹏等: "《轻金属基复合材料》", 31 December 2013, 国防工业出版社 * |
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| CN106853530A (en) * | 2017-01-13 | 2017-06-16 | 哈尔滨工业大学 | A kind of method that powdering hot pressed sintering prepares stratiform titanium matrix composite |
| CN107414086A (en) * | 2017-08-14 | 2017-12-01 | 陕西理工大学 | A kind of carbide cooperates with Strengthening and Toughening TiAl-base alloy and preparation method thereof with titanium alloy layer |
| CN108796265A (en) * | 2018-06-28 | 2018-11-13 | 北京理工大学 | A kind of preparation method of TiB nanometers of enhancing titanium matrix composite |
| CN108796265B (en) * | 2018-06-28 | 2020-06-09 | 北京理工大学 | Preparation method of TiB nano-reinforced titanium-based composite material |
| CN112063875B (en) * | 2020-09-21 | 2021-12-03 | 哈尔滨工业大学 | Method for preparing shell-like laminated structure Ti2 AlNb-based composite material by combining powder metallurgy and forging |
| CN112063875A (en) * | 2020-09-21 | 2020-12-11 | 哈尔滨工业大学 | Method for preparing shell-like laminated structure Ti2 AlNb-based composite material by combining powder metallurgy and forging |
| CN112662904A (en) * | 2020-11-23 | 2021-04-16 | 北京理工大学 | TiB and La2O3Preparation method of reinforced titanium-based composite material |
| CN112775437A (en) * | 2020-12-23 | 2021-05-11 | 西南交通大学 | Light metal-based composite material part and preparation method thereof |
| CN112775437B (en) * | 2020-12-23 | 2022-04-01 | 西南交通大学 | Light metal-based composite material part and preparation method thereof |
| CN114131015A (en) * | 2021-12-13 | 2022-03-04 | 上海交通大学 | Confined powder filling method for preparing configuration composite material |
| CN114888289A (en) * | 2022-05-10 | 2022-08-12 | 哈尔滨工业大学 | Gradient titanium-based composite material and preparation method thereof |
| CN114888289B (en) * | 2022-05-10 | 2023-09-12 | 哈尔滨工业大学 | Gradient titanium-based composite material and preparation method thereof |
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