CN106566964B - A kind of high tough bimodal distribution Al alloy composite and preparation method thereof - Google Patents

A kind of high tough bimodal distribution Al alloy composite and preparation method thereof Download PDF

Info

Publication number
CN106566964B
CN106566964B CN201611007007.1A CN201611007007A CN106566964B CN 106566964 B CN106566964 B CN 106566964B CN 201611007007 A CN201611007007 A CN 201611007007A CN 106566964 B CN106566964 B CN 106566964B
Authority
CN
China
Prior art keywords
alloy
preparation
bimodal distribution
melting
alloy composite
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
CN201611007007.1A
Other languages
Chinese (zh)
Other versions
CN106566964A (en
Inventor
成家林
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
NANJING BAOZUAN SPRING Co.,Ltd.
Original Assignee
Nanjing Institute of Technology
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Nanjing Institute of Technology filed Critical Nanjing Institute of Technology
Priority to CN201611007007.1A priority Critical patent/CN106566964B/en
Publication of CN106566964A publication Critical patent/CN106566964A/en
Application granted granted Critical
Publication of CN106566964B publication Critical patent/CN106566964B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
    • 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
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)

Abstract

The invention discloses a kind of high tough bimodal distribution Al alloy composites and preparation method thereof.The component atoms percentage expression formula of aluminium alloy of the present invention are as follows: AlaCubMgcSid, wherein 88≤a≤92,4.2≤b≤6,1.4≤c≤2,2.4≤d≤4, a+b+c+d=100.The method of above-mentioned aluminium alloy is prepared the following steps are included: choosing aluminum-system, according to phase choosing principles, alloying component is adjusted, makes it that aluminium solid solution phase can first be precipitated in process of setting, eutectic reaction then occurs, form ultra-fine eutectic structure.Bimodal distribution Al alloy composite of the invention has excellent in strength and plasticity.

Description

A kind of high tough bimodal distribution Al alloy composite and preparation method thereof
Technical field
The invention belongs to metal-base composites technology, especially a kind of high tough bimodal distribution Al alloy composite Preparation method.
Background technique
Aluminium alloy density is low, and intensity is relatively high, and near or above high-quality steel, plasticity is good, can be processed into various profiles, has The excellent performance such as excellent electric conductivity, thermal conductivity and corrosion stability, in Aeronautics and Astronautics, automobile, machine-building, ship and chemistry It is widely used in industry.But with the development of industrial technology, the mechanical property of aluminium alloy especially tensile strength is required to get over Come higher.
It is well known that refinement crystal grain is remarkably improved the intensity of metal material, the block nanometer metal developed at present Intensity is several times or even decades of times of traditional coarse-grain alloy.Therefore, developing a kind of nanocrystalline or ultra-fine grained aluminium alloy is that material is ground Study carefully the important development direction in field.In addition, the plastic deformation of block nanometer metal material be by height localized shear deformation come It realizes, the catastrophic brittle fracture without macroscopic view plastic deformation can occur at room temperature.Therefore, how to develop while having super High-intensitive and superior plasticity nanocrystalline or ultra-fine grained aluminium alloy is an extremely challenging scientific research problem.
Summary of the invention
The purpose of the present invention is to provide a kind of tough bimodal distribution Al alloy composites of novel high-strength.The knot of the aluminium alloy Structure feature is the solid solution phase of raw micro-meter scale in precipitation as cast condition using nanocrystalline or Ultra-fine Grained eutectic structure as matrix, thus Realize the good combination of superhigh intensity and superior plasticity.
The technical solution for realizing the aim of the invention is as follows: a kind of high tough bimodal distribution Al alloy composite, described Alloying component atomic percent expression formula are as follows: AlaCubMgcSid, wherein 88≤a≤92,4.2≤b≤6,1.4≤c≤2, 2.4≤d≤4, a+b+c+d=100.
The invention also discloses the preparation methods of the tough bimodal distribution Al alloy composite of the height, including following step It is rapid:
Step 1: being matched according to the predetermined ingredient of composite material, alloying component atomic percent expression formula are as follows: AlaCubMgcSid, wherein 88≤a≤92,4.2≤b≤6,1.4≤c≤2,2.4≤d≤4, a+b+c+d=100.
Step 2: tri- kinds of raw materials of Al, Cu, Si are smelted into uniformly under argon atmosphere using non-consumable arc furnace Intermediate alloy.
Step 3: above-mentioned intermediate alloy and pure magnesium raw material are put into graphite crucible, used under argon atmosphere Induction melting, alloy is heated and is melted, and melting is uniform.
Step 4: the uniform alloy solution of melting is cast in copper mold, obtaining, there is the aluminium of tough bimodal distribution structure to close Metal/composite material profile.Mechanical properties >=600MPa of the Al alloy composite, stretching plastic strain >=8%.
Compared with prior art, the present invention its remarkable advantage: it is tough bimodal that the present invention has developed a kind of novel high-strength for the first time It is distributed Al alloy composite.The composite material has unique design feature, is with nanocrystalline or Ultra-fine Grained eutectic structure The solid solution phase of raw micro-meter scale in as cast condition is precipitated, to realize the good combination of superhigh intensity and superior plasticity in matrix.
Detailed description of the invention
Fig. 1 is the flow chart for Al alloy composite of the present invention preparation.
Fig. 2 is the microstructure of the high tough bimodal distribution Al alloy composite of embodiment 2.
Fig. 3 is the room temperature tensile load-deformation curve of the high tough bimodal distribution Al alloy composite of embodiment 1.
Specific embodiment
(1) design of alloy:
The Al-Cu-Mg-Si alloy system with good glass forming ability (GFA) is selected, according to phase choosing principles, two First alloy phase diagram determines alloying component, obtains required alloy component range, AlaCubMgcSid, wherein 88≤a≤92,4.2≤b ≤ 6,1.4≤c≤2,2.4≤d≤4, a+b+c+d=100.
(2) alloy melting:
The atomic percent between obtained different-alloy element, which is designed, according to (1) ingredient converses mass percent, Required alloy is configured using high pure metal constituent element.Using non-consumable arc furnace, by Al, Cu, Si under argon atmosphere Three kinds of raw materials are smelted into uniform intermediate alloy.Above-mentioned intermediate alloy and pure magnesium raw material are put into graphite crucible, in argon gas Induction melting is used under protective atmosphere, alloy is heated and is melted, and melting is uniform.
(3) material forms:
The uniform alloy solution of melting is cast in copper mold, the aluminium alloy compound material with tough bimodal distribution structure is obtained Expect profile, shape and size can as needed be designed the inner cavity of copper mold.
(4) structural characterization:
Conjunction using X-ray diffractometer (XRD), optical microscopy (OM) and electronic scanner microscope (SEM) etc. to preparation Gold carries out Microstructure characterization, and further carries out mechanical property characterization to it, has best comprehensive mechanical property to determine Alloying component.
The present invention is further explained in the light of specific embodiments.
Embodiment 1
(1) selection of raw material
The present invention prepares the purity such as table 1 of each metal constituent element of master alloy ingot selection, alloying component Al90Cu5.1Mg1.7S i3.2(atomic percent).
Table 1 prepares the purity (%) that master alloy ingot selects metal constituent element
(2) melting of alloy
Induction melting is used under argon atmosphere, specific procedure is as follows:
A, after the oxide skin that the surface mechanical grinding of raw metal is removed to surface, according to composition proportion first by Al, Cu, Si Raw material using non-consumable arc furnace melting 2 ~ 3 times, and applies function composite by electromagnetic stirring under argon atmosphere, and it is equal to obtain mixing Even master alloy button ingot.The electric current used when melting is 300 ~ 350A, and the voltage that electromagnetic agitation uses is 1 ~ 3V.
B, above-mentioned intermediate alloy and pure magnesium raw material are put into graphite crucible, are heated to 750 ~ 800 using induction melting furnace DEG C, keep the temperature 20 ~ 30 minutes.
(3) material forms
The uniform alloy solution of melting is cast in copper mold, the aluminium alloy compound material with tough bimodal distribution structure is obtained Expect profile, shape and size can as needed be designed the inner cavity of copper mold.
(4) structure and performance characterization
Fig. 3 is high tough bimodal distribution Al alloy composite room temperature tensile load-deformation curve, experiment condition are as follows: sample For product gauge length having a size of 3 × 15mm, experimental temperature is room temperature (25 DEG C), and compression strain rate is 2 × 10-4s-1.Mechanical property is surveyed Test result shows: prepared composite material tensile strength has reached 660MPa, stretching plastic 10%.
Embodiment 2
Using method same as Example 1, alloying component Al88Cu6Mg2Si4, it is prepared for the conjunction of 10mm bimodal distribution aluminium Metal/composite material, tensile strength have reached 720MPa, and stretching plastic strain has reached 8%.
Fig. 2 is the 10mm diameter Al using the preparation of above-mentioned process conditions88Cu6Mg2Si4The microstructure of alloy can be seen Out, the structure of the composite material are as follows: the α-Al solid solution phase of micro-meter scale is uniform-distribution on the matrix of ultra-fine eutectic structure.
Embodiment 3
Using method same as Example 1, alloying component Al92Cu4.2Mg1.4Si2.4, it is prepared for 10mm bimodal distribution Al alloy composite, tensile strength have reached 610MPa, and stretching plastic strain has reached 12%.
Facts proved that using simple casting technique, bimodal distribution Al alloy composite of the invention realize intensity and The good combination of plasticity.

Claims (6)

1. a kind of high tough bimodal distribution Al alloy composite, it is characterised in that the alloying component atomic percent expression Formula are as follows: AlaCubMgcSid, wherein 88≤a≤92,4.2≤b≤6,1.4≤c≤2,2.4≤d≤4, a+b+c+d=100.
2. a kind of preparation method of high tough bimodal distribution Al alloy composite, it is characterised in that the following steps are included:
Step 1: being matched according to the predetermined ingredient of composite material, alloying component atomic percent expression formula are as follows: AlaCubMgcSid, wherein 88≤a≤92,4.2≤b≤6,1.4≤c≤2,2.4≤d≤4, a+b+c+d=100；
Step 2: tri- kinds of raw materials of Al, Cu, Si are smelted into uniform under argon atmosphere using non-consumable arc furnace Between alloy；
Step 3: above-mentioned intermediate alloy and pure magnesium raw material are put into graphite crucible, using induction under argon atmosphere Melting, alloy is heated and is melted, and melting is uniform；
Step 4: the uniform alloy solution of melting is cast in copper mold, obtaining has the aluminium alloy of tough bimodal distribution structure multiple Condensation material profile.
3. the preparation method of Al alloy composite according to claim 2, it is characterised in that: the alloy constituent element it is pure Degree >=99.5%.
4. the preparation method of Al alloy composite according to claim 3, it is characterised in that: used when second step melting Electric current be 300 ~ 350A, the voltage that electromagnetic agitation uses is 1 ~ 3V.
5. the preparation method of Al alloy composite according to claim 4, it is characterised in that: third step induction melting Heating temperature is 750-800 DEG C, keeps the temperature 20-30 minutes.
6. the preparation method of Al alloy composite according to claim 5, it is characterised in that: the aluminium alloy compound material Mechanical properties >=600MPa of material, stretching plastic strain >=8%.
CN201611007007.1A 2016-11-16 2016-11-16 A kind of high tough bimodal distribution Al alloy composite and preparation method thereof Active CN106566964B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN201611007007.1A CN106566964B (en) 2016-11-16 2016-11-16 A kind of high tough bimodal distribution Al alloy composite and preparation method thereof

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201611007007.1A CN106566964B (en) 2016-11-16 2016-11-16 A kind of high tough bimodal distribution Al alloy composite and preparation method thereof

Publications (2)

Publication Number Publication Date
CN106566964A CN106566964A (en) 2017-04-19
CN106566964B true CN106566964B (en) 2019-01-25

Family

ID=58542022

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201611007007.1A Active CN106566964B (en) 2016-11-16 2016-11-16 A kind of high tough bimodal distribution Al alloy composite and preparation method thereof

Country Status (1)

Country Link
CN (1) CN106566964B (en)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111519073B (en) * 2020-06-03 2021-07-09 上海鑫烯复合材料工程技术中心有限公司 Nano carbon reinforced metal matrix composite material with trimodal characteristics

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH01191759A (en) * 1988-01-26 1989-08-01 Toyota Motor Corp Aluminum alloy composite material
JPH03264638A (en) * 1990-03-13 1991-11-25 Furukawa Alum Co Ltd Aluminum alloy high damping material
CN101348869B (en) * 2007-07-16 2010-06-02 南京理工大学 Preparation of crystal grain size controllable bimodal distribution block superfine/nanocrystalline alloy
CN104178663B (en) * 2013-05-27 2016-10-05 中国科学院金属研究所 For preparing aluminum-based alloy material of disintegrate pressure break ball and preparation method thereof
CN105331858A (en) * 2015-11-20 2016-02-17 江苏大学 Preparation method for high-strength and high-toughness ultra-fine grain aluminium alloy

Also Published As

Publication number Publication date
CN106566964A (en) 2017-04-19

Similar Documents

Publication Publication Date Title
Pourbahari et al. Toward unraveling the effects of intermetallic compounds on the microstructure and mechanical properties of Mg–Gd–Al–Zn magnesium alloys in the as-cast, homogenized, and extruded conditions
Li et al. Effect of heat treatment on AlSi10Mg alloy fabricated by selective laser melting: Microstructure evolution, mechanical properties and fracture mechanism
Attar et al. Selective laser melting of in situ titanium–titanium boride composites: Processing, microstructure and mechanical properties
Tahamtan et al. Fabrication of Al/A206–Al2O3 nano/micro composite by combining ball milling and stir casting technology
Shi et al. Effects of Sc addition on the microstructure and mechanical properties of cast Al-3Li-1.5 Cu-0.15 Zr alloy
Han et al. In situ TiB2 particulate reinforced near eutectic Al–Si alloy composites
Lagos et al. Fabrication and characterisation of titanium matrix composites obtained using a combination of self propagating high temperature synthesis and spark plasma sintering
Zhang et al. Ductile ultrafine-grained Ti-based alloys with high yield strength
Qin et al. Effect of modification and aging treatment on mechanical properties of Mg2Si/Al composite
Jayalakshmi et al. Development of novel Mg–Ni60Nb40 amorphous particle reinforced composites with enhanced hardness and compressive response
Sankaranarayanan et al. Effect of nanoscale boron carbide particle addition on the microstructural evolution and mechanical response of pure magnesium
Oskooie et al. Microstructure, plastic deformation and strengthening mechanisms of an Al–Mg–Si alloy with a bimodal grain structure
Zhang et al. A novel fabrication technology of in situ TiB2/6063Al composites: high energy ball milling and melt in situ reaction
Sankaranarayanan et al. Development of high performance magnesium composites using Ni50Ti50 metallic glass reinforcement and microwave sintering approach
Zhou et al. Simultaneously increasing the strength and ductility of nano-sized TiN particle reinforced Al–Cu matrix composites
Zhao et al. Effects of friction stir processing on the microstructure and superplasticity of in situ nano-ZrB2/2024Al composite
Guo et al. Achieving high-strength magnesium matrix nanocomposite through synergistical effect of external hybrid (SiC+ TiC) nanoparticles and dynamic precipitated phase
Fazakas et al. Effect of iron content on the structure and mechanical properties of Al25Ti25Ni25Cu25 and (AlTi) 60-xNi20Cu20Fex (x= 15, 20) high-entropy alloys
Xie et al. Designing new low alloyed Mg—RE alloys with high strength and ductility via high-speed extrusion
Pan et al. Enhanced strength and ductility of nano-TiBw-reinforced titanium matrix composites fabricated by electron beam powder bed fusion using Ti6Al4V–TiBw composite powder
EP2885437B1 (en) Al-nb-b master alloy for grain refining
WO2013115490A1 (en) Magnesium alloy having high ductility and high toughness, and preparation method thereof
Emamy et al. The influence of Ni addition and hot-extrusion on the microstructure and tensile properties of Al–15% Mg2Si composite
Rashad et al. Room temperature mechanical properties of Mg–Cu–Al alloys synthesized using powder metallurgy method
Yeganeh et al. The influence of Cu–15P master alloy on the microstructure and tensile properties of Al–25 wt% Mg2Si composite before and after hot-extrusion

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant
TR01 Transfer of patent right

Effective date of registration: 20220114

Address after: No. 92, Xinqiao village, Taocun village, Jingqiao Town, Lishui District, Nanjing, Jiangsu 210008

Patentee after: NANJING BAOZUAN SPRING Co.,Ltd.

Address before: 1 No. 211167 Jiangsu city of Nanjing province Jiangning Science Park Hongjing Road

Patentee before: NANJING INSTITUTE OF TECHNOLOGY

TR01 Transfer of patent right