CN109797326A - A kind of high strength heat resistant alloy and preparation method thereof - Google Patents
A kind of high strength heat resistant alloy and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a kind of high strength heat resistant alloy and preparation method thereof, the alloying element weight percent expression formulas are as follows: AlaCubMncCedNieZrf, wherein 83.75≤a≤89.9,7.0≤b≤9.0,0.5≤c≤2.0,1.0≤d≤2.5,1.5≤e≤2.5,0.1≤f≤0.25, a+b+c+d+e+f=100.It the steps include: selection heat-resisting aluminium alloy system, alloying component adjusted according to alloy graining path, prepares alloy pig, alloy pig flat-die forging, forging stock is dissolved and aging strengthening model, obtain a kind of structure organization that foreign lands strengthen across scale, i.e. the heat-resisting phase of nanoscale intermetallic compound is precipitated equably to strengthen matrix in intra-die, compound is distributed between the heating resisting metal of micro-meter scale on crystal boundary continuously and uniformly to stablize crystal boundary, material has excellent Testing Tensile Strength at Elevated Temperature and elongation percentage.The tensile strength of 400 DEG C of the alloy material reaches 116MPa, and elongation percentage reaches 37.5%, and compared with active service ZL208 alloy (T6), tensile strength promotes 31.8%, and elongation percentage improves 2.5 times.
Description
Technical field
The invention belongs to heat-resistant aluminium alloy material technology, especially a kind of High-strength heat-resistant aluminum alloy material and its preparation side
Method.
Background technique
In face of resource, the energy, environment severe challenge under, the manufacturing industry such as aircraft, automobile in order to reduce energy consumption, save money
Source, protection environment, it is more more and more urgent to the high-performance and lightweight requirements of structure material.Aluminium and aluminium alloy have density it is small,
Intensity is high, processing performance is good, many merits such as corrosion-resistant, as excellent structural material, be widely used in space flight and aviation,
It builds a bridge, the various fields such as automobile ship, mechanical equipment.Wherein, heat-resisting aluminium alloy have excellent high-temperature oxidation resistance and
There are preferable plasticity_resistant deformation ability and yield strength at temperature and dynamic static load long duration of action, is widely used to soldier
Device, aerospace, the engine piston of automobile ship, especially tank, cylinder sleeve, cabinet, shell, the aero-engine gas of guided missile
Cylinder, blade, aircraft skin etc..As the development of aerospace, weapon plate armour is higher to the high-temperature behavior proposition of heat-resisting aluminium alloy
Requirement, however the performances such as the heat fatigue of the cast aluminium alloy material of active service, high temperature resistant have closed on limiting condition, are difficult to adapt to dress
Standby growth requirement.Such as the piston of engine, as one of engine chamber critical component, the operating time time is exposed to 350
In~400 DEG C of environment of high temperature gas, thermal mechanical fatigue effect is furthermore still suffered from.Ingot casting production method is simultaneously widely applied
Heat-resisting phase volume fraction is less in the heat-resisting aluminium alloys such as ZL208, and strengthening effect is insufficient, can only meet in 350 DEG C of temperature below
It uses.Although the service temperature of ZL207 alloy reaches 400 DEG C, the heat-resisting coupling embrittlement of a large amount of fine mesh at the grain boundaries
Property, cause it too low in 350 DEG C ~ 400 DEG C of plasticity, the titanium alloy of 350 ~ 400 DEG C of temperature ranges can not be substituted, it is impossible to meet
Light-weighted demand for development.In addition, it is lower to often lead to material plasticity because interface bond strength is limited for composite material.
Summary of the invention
The purpose of the present invention is to provide a kind of High-strength heat-resistant aluminum alloy materials.The material not only has high at high temperature
Tensile strength, and have excellent plasticity.Material preparation process is simple, at low cost, easy to spread and universal.
The technical solution for realizing the aim of the invention is as follows: a kind of High-strength heat-resistant aluminum alloy material, alloy member
Plain weight percent expression formula are as follows: AlaCubMncCedNieZrf, wherein 83.75≤a≤89.9,7.0≤b≤9.0,0.5
≤ c≤2.0,1.0≤d≤2.5,1.5≤e≤2.5,0.1≤f≤0.25, a+b+c+d+e+f=100.
Further, the tissue signature of the High-strength heat-resistant aluminum alloy material is: nanoscale is equably precipitated in intra-die
Intermetallic compound Al20Cu2Mn3、Al2Cu heat-resisting phase is precipitated on crystal boundary between the micron order heating resisting metal of continuous uniform distribution and changes
Close object Al16Cu4Mn2Ce、Al7Cu4Ni, the structure organization strengthened with foreign lands across scale.
Further, the material have 400 DEG C excellent of tensile strength reach 105 ~ 117MPa and elongation percentage 29% ~
38%。
It is a kind of to prepare above-mentioned heat-resistance high-strength aluminum alloy materials method, comprising the following steps:
Step 1: heat-resisting aluminium alloy system is chosen, according to solidification phasor, Ala1Cub1Mnc1Ced1Quaternary alloy richness aluminium end, wherein
81.0≤a1≤ 94.0,5.0≤b1≤ 14.0,0.5≤c1≤ 2.0,0.5≤d1≤ 3.0, Al is precipitated16Cu4Mn2Ce、
Al20Cu2Mn3、Al2Cu phase, Ala2Cub2Nic2Ternary alloy three-partalloy richness aluminium end, wherein 78.0≤a2< 96.0,4.0≤b2≤ 12.0,0
< c2≤ 10.0, Al is precipitated7Cu4Ni phase adjusts alloying component according to quaternary alloy richness aluminium end and ternary alloy three-partalloy richness aluminium end
AlaCubMncCedNieZrf, wherein 83.75≤a≤89.9,7.0≤b≤9.0,0.5≤c≤2.0,1.0≤d≤2.5,1.5
≤ e≤2.5,0.1≤f≤0.25, a+b+c+d+e+f=100 make its crystal boundary in process of setting that micro-meter scale equably be precipitated
Al16Cu4Mn2Ce、Al7Cu4Nanoscale intermetallic compound is equably precipitated in crystal grain in Ni intermetallic compound phase
Al20Cu2Mn3、Al2Cu phase；
Step 2: after the surface mechanical grinding of raw metal to be removed to the oxide skin on surface, it is standby according to the composition proportion of the first step
Material；
Step 3: sequentially adding high-purity Al, Cu, Ni, Mn, Zr, Al-10%Ce, Al into water jacketed copper crucible, covers bell and take out very
Sky is to 2 × 10-2Pa is filled with the high-purity argon gas (99.99%) of 0.4 ~ 0.6MPa into furnace, using water jacketed copper crucible suspension smelting furnace
Molten alloy ingot；
Step 4: 3 ~ 4 passage of molten alloy, obtains uniformly mixed alloy pig；
Step 5: carry out flat-die forging to alloy pig, 500 DEG C of initial forging temperature, 400 DEG C of final forging temperature, each deflection 20 ~
30%, total deformation is crushed coarse precipitated phase 60 ~ 70%, obtains uniform formation；
Step 6: forging stock is dissolved 12 hours at 540 DEG C ± 5 DEG C, in 25 DEG C of water of quenching；
Step 7: again 175 DEG C ± 5 timeliness 5 hours, it is air-cooled.
Further, in second step, raw metal purity is greater than 99.5%.
Further, in the 4th step, monitor system 18-22KW.
Compared with prior art, the present invention its remarkable advantage is: (1) present invention devises a kind of across scale reinforcing of foreign lands
Structure organization, i.e., the intermetallic compound phase that micro-meter scale is precipitated on crystal boundary form continuous net-shaped structure to stablize crystal boundary, crystal grain
Compound improves the mechanical behavior under high temperature of material significantly, makes material mutually with stabilized matrix between interior uniform precipitation nano level metal
Material meets high-temperature service condition.(2) material under high temperature has excellent plasticity.Heat-resisting aluminium alloy introduces continuous equal in the present invention
The intermetallic compound phase of even distribution is conducive to compatibility of deformation and carries out, material is made to have excellent plasticity.
Detailed description of the invention
Fig. 1 is heat-resistant aluminium alloy material preparation flow figure of the present invention.
Fig. 2 is 1 heat-resistant aluminium alloy material macrograph of embodiment.
Fig. 3 is micro-organization chart's (micron meter that a is distributed for continuous uniform on crystal boundary of 1 heat-resistant aluminium alloy material of embodiment
Spend Al7Cu4Ni phase and Al16Cu4Mn2Ce phase, b are the equally distributed nanoscale Al of intra-die20Cu2Mn3Phase, c are in crystal grain
The equally distributed nanoscale Al in portion2Cu phase).
Fig. 4 is high temperature (400 DEG C) stress strain curve figure of 1 heat-resistant aluminium alloy material of embodiment.
Specific embodiment
The preparation step of following embodiment is as shown in the flow diagram of Fig. 1.
Embodiment 1
(1) alloying component selects
Heat-resisting aluminium alloy system is chosen, according to solidification phasor, Ala1Cub1Mnc1Ced1Quaternary alloy richness aluminium end (81.0≤a1≤
94.0,5.0≤b1≤ 14.0,0.5≤c1≤ 2.0,0.5≤d1≤ 3.0) Al is precipitated16Cu4Mn2Ce、Al20Cu2Mn3、Al2Cu phase,
Ala2Cub2Nic2Ternary alloy three-partalloy richness aluminium end (78.0≤a2< 96.0,4.0≤b2≤ 12.0,0 < c2≤ 10.0) Al is precipitated7Cu4Ni
Thus phase adjusts this alloying component Al86.1Cu8.3Mn1.0Ce2.4Ni2.0Zr0.2；
(2) selection of raw material
Purity such as table 1, the alloying component of each metal constituent element that the present invention prepares alloy pig selection be
Al86.1Cu8.3Mn1.0Ce2.4Ni2.0Zr0.2(weight percent)；
Table 1 prepares the purity (%) that alloy pig selects metal constituent element
| Alloying element | Al | Cu | Mn | Zr | Ni | Al-10%Ce |
| Purity/% | 99.9 | 99.99 | 99.9 | 99.9 | 99.9 | 99.5 |
(3) preparation of alloy
Using water jacketed copper crucible suspension smelting furnace molten alloy ingot, specific procedure is as follows:
A, it after the oxide skin that the surface mechanical grinding of raw metal is removed to surface, stocks up according to designed composition proportion；It presses
In the water jacketed copper crucible that the material prepared is put into smelting furnace according to the weight of every ingot 60g or so, cover bell be evacuated to 2 ×
10-2Pa；The high-purity argon gas (99.99%) of a certain amount of pressure is filled with into furnace, argon pressure range is 0.4MPa；
B, multi-pass molten alloy ingot obtains uniformly mixed alloy pig.The power used when melting is 20KW；
(4) flat-die forging of alloy pig
To alloy pig carry out flat-die forging, 500 DEG C ± 5 DEG C of initial forging temperature, 400 DEG C ± 10 DEG C of final forging temperature, each deflection control
System is 20 ~ 30%, and total deformation is 60 ~ 70%；
(5) heat treatment of forging stock
A, alloy is dissolved 12 hours at 540 DEG C ± 5 DEG C, in 25 DEG C of water of quenching；
B, alloy 170 DEG C ± 5 DEG C timeliness 5 hours, it is air-cooled；
(6) tissue, performance test
The pictorial diagram of material prepared is as shown in Figure 2.Fine Texture of Material is as shown in Figure 3: obtaining what foreign lands strengthened across scale
Structure organization is continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce phase, in crystal grain
The Al of nanoscale is precipitated evenly20Cu2Mn3、Al2Cu phase.
The tensile stress-strain curve that Fig. 4 is 400 DEG C of heat-resistant aluminium alloy material, mechanical experimental results show: made
Standby Tensile strength reaches 116MPa, improves 31.8% than ZL208 alloy, and plasticity reaches 37.5%, is ZL208 alloy
3.5 again.
Embodiment 2
(1) alloying component selects
Heat-resisting aluminium alloy system is chosen, according to solidification phasor, Ala1Cub1Mnc1Ced1Quaternary alloy richness aluminium end (81.0≤a1≤
94.0,5.0≤b1≤ 14.0,0.5≤c1≤ 2.0,0.5≤d1≤ 3.0) Al is precipitated16Cu4Mn2Ce、Al20Cu2Mn3、Al2Cu phase,
Ala2Cub2Nic2Ternary alloy three-partalloy richness aluminium end (78.0≤a2< 96.0,4.0≤b2≤ 12.0,0 < c2≤ 10.0) Al is precipitated7Cu4Ni
Phase adjusts this alloying component Al86.4Cu8.4Mn1.2Ce2.3Ni1.5Zr0.2；
(2) selection of raw material
Purity such as table 1, the alloying component of each metal constituent element that the present invention prepares alloy pig selection be
Al86.4Cu8.4Mn1.2Ce2.3Ni1.5Zr0.2(weight percent)；
Table 1 prepares the purity (%) that alloy pig selects metal constituent element
| Alloying element | Al | Cu | Mn | Zr | Ni | Al-10%Ce |
| Purity/% | 99.9 | 99.99 | 99.9 | 99.9 | 99.9 | 99.5 |
(3) preparation of alloy
Using water jacketed copper crucible suspension smelting furnace molten alloy ingot, specific procedure is as follows:
A, it after the oxide skin that the surface mechanical grinding of raw metal is removed to surface, stocks up according to designed composition proportion；It presses
In the water jacketed copper crucible that the material prepared is put into smelting furnace according to the weight of every ingot 60g or so, cover bell be evacuated to 2 ×
10-2Pa；The high-purity argon gas (99.99%) of a certain amount of pressure is filled with into furnace, argon pressure range is 0.4MPa；
B, multi-pass molten alloy ingot obtains uniformly mixed alloy pig.The power used when melting is 19kW；
(4) flat-die forging of alloy pig
To alloy pig carry out flat-die forging, 500 DEG C ± 5 DEG C of initial forging temperature, 400 DEG C ± 10 DEG C of final forging temperature, each deflection control
System is 20 ~ 30%, and total deformation is 60 ~ 70%；
(5) heat treatment of forging stock
A, alloy is dissolved 12 hours at 540 DEG C ± 5 DEG C, in 25 DEG C of water of quenching；
B, alloy 175 DEG C ± 5 DEG C timeliness 5 hours, it is air-cooled；
(6) tissue, performance test
The structure organization that foreign lands strengthen across scale is obtained, i.e., is continuously and uniformly distributed micro-meter scale at grain boundaries
Al7Cu4Ni and Al16Cu4Mn2The Al of nanoscale is equably precipitated in crystal grain for Ce phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 114MPa, compares ZL208
Alloy improves 29.5%, and plasticity reaches 38.0%, is 3.6 times of ZL208 alloy.
Embodiment 3
(1) alloying component selects
Heat-resisting aluminium alloy system is chosen, according to solidification phasor, Ala1Cub1Mnc1Ced1Quaternary alloy richness aluminium end (81.0≤a1≤
94.0 5.0≤b1≤ 14.0,0.5≤c1≤ 2.0,0.5≤d1≤ 3.0) Al is precipitated16Cu4Mn2Ce、Al20Cu2Mn3、Al2Cu phase,
Ala2Cub2Nic2Ternary alloy three-partalloy richness aluminium end (78.0≤a2< 96.0,4.0≤b2≤ 12.0,0 < c2≤ 10.0) Al is precipitated7Cu4Ni
Phase adjusts this alloying component Al83.75Cu9.0Mn2.0Ce2.5Ni2.5Zr0.25；
(2) selection of raw material
The present invention prepares the purity such as table 1 of each metal constituent element of alloy pig selection, alloying component Al83.75Cu9.0Mn2.0Ce2.5
Ni2.5Zr0.25(weight percent)；
Table 1 prepares the purity (%) that alloy pig selects metal constituent element
| Alloying element | Al | Cu | Mn | Zr | Ni | Al-10%Ce |
| Purity/% | 99.9 | 99.99 | 99.9 | 99.9 | 99.9 | 99.5 |
(3) preparation of alloy
Using water jacketed copper crucible suspension smelting furnace molten alloy ingot, specific procedure is as follows:
A, it after the oxide skin that the surface mechanical grinding of raw metal is removed to surface, stocks up according to designed composition proportion；It presses
In the water jacketed copper crucible that the material prepared is put into smelting furnace according to the weight of every ingot 60g or so, cover bell be evacuated to 2 ×
10-2Pa；The high-purity argon gas (99.99%) of a certain amount of pressure is filled with into furnace, argon pressure range is 0.6MPa；
B, multi-pass molten alloy ingot obtains uniformly mixed alloy pig.The power used when melting is 22KW；
(4) flat-die forging of alloy pig
To alloy pig carry out flat-die forging, 500 DEG C ± 5 DEG C of initial forging temperature, 400 DEG C ± 10 DEG C of final forging temperature, each deflection control
System is 20 ~ 30%, and total deformation is 60 ~ 70%；
(5) heat treatment of forging stock
A, alloy is dissolved 12 hours at 540 DEG C ± 5 DEG C, in 25 DEG C of water of quenching；
B, alloy 175 DEG C ± 5 DEG C timeliness 5 hours, it is air-cooled；
(6) tissue, performance test
The structure organization that foreign lands strengthen across scale is obtained, i.e., is continuously and uniformly distributed micro-meter scale at grain boundaries
Al7Cu4Ni and Al16Cu4Mn2The Al of nanoscale is equably precipitated in crystal grain for Ce phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 117MPa, compares ZL208
Alloy improves 33.0%, and plasticity reaches 32.5%, is 3.0 times of ZL208 alloy.
Embodiment 4
It is Al that the present invention, which prepares master alloy ingredient,85.9Cu8.0Mn1.0Ce2.5Ni2.5Zr0.1(weight percent), obtain foreign lands across
The structure organization that scale is strengthened, i.e., be continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce
The Al of nanoscale is equably precipitated in crystal grain for phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 113MPa, compares ZL208
Alloy improves 28.4%, and plasticity reaches 36.5%, is 3.4 times of ZL208 alloy.
Embodiment 5
It is Al that the present invention, which prepares master alloy ingredient,88.75Cu7.0Mn1.0Ce1.0Ni2.1Zr0.15(weight percent), obtain foreign lands across
The structure organization that scale is strengthened, i.e., be continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce
The Al of nanoscale is equably precipitated in crystal grain for phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 109MPa, compares ZL208
Alloy improves 23.9%, and plasticity reaches 35.8%, is 3.3 times of ZL208 alloy.
Embodiment 6
It is Al that the present invention, which prepares master alloy ingredient,89.9Cu7.0Mn0.5Ce1.0Ni1.5Zr0.1(weight percent), obtain foreign lands across
The structure organization that scale is strengthened, i.e., be continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce
The Al of nanoscale is equably precipitated in crystal grain for phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 105MPa, compares ZL208
Alloy improves 19.3%, and plasticity reaches 37.0%, is 3.5 times of ZL208 alloy.
Embodiment 7
It is Al that the present invention, which prepares master alloy ingredient,86.7Cu8.0Mn1.5Ce1.5Ni2.2Zr0.1(weight percent), obtain foreign lands across
The structure organization that scale is strengthened, i.e., be continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce
The Al of nanoscale is equably precipitated in crystal grain for phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 113MPa, compares ZL208
Alloy improves 28.4%, and plasticity reaches 35.2%, is 3.3 times of ZL208 alloy.
Embodiment 8
It is Al that the present invention, which prepares master alloy ingredient,85.55Cu8.5Mn1.5Ce2.0Ni2.3Zr0.15(weight percent), obtain foreign lands across
The structure organization that scale is strengthened, i.e., be continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce
The Al of nanoscale is equably precipitated in crystal grain for phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 115MPa, compares ZL208
Alloy improves 30.7%, and plasticity reaches 32.1%, is 3.0 times of ZL208 alloy.
Embodiment 9
It is Al that the present invention, which prepares master alloy ingredient,85.2Cu8.6Mn2.0Ce2.0Ni2.0Zr0.2(weight percent), obtain foreign lands across
The structure organization that scale is strengthened, i.e., be continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce
The Al of nanoscale is equably precipitated in crystal grain for phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 116MPa, compares ZL208
Alloy improves 31.8%, and plasticity reaches 29.1%, is 2.7 times of ZL208 alloy.
Embodiment 10
It is Al that the present invention, which prepares master alloy ingredient,84.4Cu9.0Mn2.0Ce2.5Ni2.0Zr0.2(weight percent), obtain foreign lands across
The structure organization that scale is strengthened, i.e., be continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce
The Al of nanoscale is equably precipitated in crystal grain for phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 112MPa, compares ZL208
Alloy improves 27.3%, and plasticity reaches 30.5%, is 2.85 times of ZL208 alloy.
Embodiment 11
It is Al that the present invention, which prepares master alloy ingredient,87.8Cu7.5Mn1.0Ce1.5Ni2.0Zr0.2(weight percent), obtain foreign lands across
The structure organization that scale is strengthened, i.e., be continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce
The Al of nanoscale is equably precipitated in crystal grain for phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 110MPa, compares ZL208
Alloy improves 25.0%, and plasticity reaches 30.1%, is 2.8 times of ZL208 alloy.
Embodiment 12
It is Al that the present invention, which prepares master alloy ingredient,86.8Cu8.0Mn1.0Ce2.0Ni2.0Zr0.2(weight percent), obtain foreign lands across
The structure organization that scale is strengthened, i.e., be continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce
The Al of nanoscale is equably precipitated in crystal grain for phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 112MPa, compares ZL208
Alloy improves 27.3%, and plasticity reaches 31.3%, is 2.9 times of ZL208 alloy.
Embodiment 13
It is Al that the present invention, which prepares master alloy ingredient,86.8Cu7.5Mn1.5Ce2.0Ni2.0Zr0.2(weight percent), obtain foreign lands across
The structure organization that scale is strengthened, i.e., be continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce
The Al of nanoscale is equably precipitated in crystal grain for phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 109MPa, compares ZL208
Alloy improves 23.9%, and plasticity reaches 29.3%, is 2.7 times of ZL208 alloy.
Embodiment 14
It is Al that the present invention, which prepares master alloy ingredient,84.8Cu8.8Mn1.5Ce2.2Ni2.5Zr0.2(weight percent), obtain foreign lands across
The structure organization that scale is strengthened, i.e., be continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce
The Al of nanoscale is equably precipitated in crystal grain for phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 115MPa, compares ZL208
Alloy improves 30.7%, and plasticity reaches 30.8%, is 2.8 times of ZL208 alloy.
Embodiment 15
It is Al that the present invention, which prepares master alloy ingredient,86.8Cu7.5Mn1.5Ce2.0Ni2.0Zr0.2(weight percent), obtain foreign lands across
The structure organization that scale is strengthened, i.e., be continuously and uniformly distributed the Al of micro-meter scale at grain boundaries7Cu4Ni and Al16Cu4Mn2Ce
The Al of nanoscale is equably precipitated in crystal grain for phase20Cu2Mn3、Al2Cu phase.
Mechanical experimental results show: the tensile strength at prepared 400 DEG C of material reaches 114MPa, compares ZL208
Alloy improves 29.5%, and plasticity reaches 31.2%, is 2.9 times of ZL208 alloy.
Claims (9)
1. a kind of High-strength heat-resistant aluminum alloy material, which is characterized in that its alloying element weight percent expression formula are as follows:
AlaCubMncCedNieZrf, wherein 83.75≤a≤89.9,7.0≤b≤9.0,0.5≤c≤2.0,1.0≤d≤2.5,1.5
≤ e≤2.5,0.1≤f≤0.25, a+b+c+d+e+f=100.
2. High-strength heat-resistant aluminum alloy material as described in claim 1, which is characterized in that the aluminum alloy materials have foreign lands across ruler
Spend the structure organization strengthened.
3. High-strength heat-resistant aluminum alloy material as claimed in claim 1 or 2, which is characterized in that the tissue of the aluminum alloy materials is special
Sign is: nanoscale intermetallic compound Al is equably precipitated in intra-die20Cu2Mn3、Al2Cu heat-resisting phase is precipitated on crystal boundary
Compound Al between the micron order heating resisting metal of continuous uniform distribution16Cu4Mn2Ce、Al7Cu4Ni。
4. High-strength heat-resistant aluminum alloy material a method according to any one of claims 1-3, which is characterized in that the material has excellent
400 DEG C of tensile strength reaches 105 ~ 117MPa and elongation percentage 29% ~ 38%.
5. a kind of method for preparing heat-resistance high-strength aluminum alloy materials, comprising the following steps:
Step 1: choosing heat-resisting aluminium alloy system, according to quaternary alloy richness aluminium end and ternary alloy three-partalloy richness aluminium end, alloying component is adjusted
AlaCubMncCedNieZrf, 83.75≤a≤89.9,7.0≤b≤9.0,0.5≤c≤2.0,1.0≤d≤2.5,1.5≤e≤
2.5,0.1≤f≤0.25, a+b+c+d+e+f=100 make its crystal boundary in process of setting that micro-meter scale equably be precipitated
Al16Cu4Mn2Ce、Al7Cu4Nanoscale intermetallic compound is equably precipitated in crystal grain in Ni intermetallic compound phase
Al20Cu2Mn3、Al2Cu phase, wherein according to solidification phasor, Ala1Cub1Mnc1Ced1Quaternary alloy richness aluminium end, 81.0≤a1≤
94.0,5.0≤b1≤ 14.0,0.5≤c1≤ 2.0,0.5≤d1≤ 3.0, Al is precipitated16Cu4Mn2Ce、Al20Cu2Mn3、Al2Cu phase,
Ala2Cub2Nic2Ternary alloy three-partalloy richness aluminium end, 78.0≤a2< 96.0,4.0≤b2≤ 12.0,0 < c2≤ 10.0, Al is precipitated7Cu4Ni
Phase；
Step 2: after the surface mechanical grinding of raw metal to be removed to the oxide skin on surface, it is standby according to the composition proportion of the first step
Material；
Step 3: sequentially adding high-purity Al, Cu, Ni, Mn, Zr, Al-10%Ce, Al into water jacketed copper crucible, covers bell and take out very
Sky is to 2 × 10-2Pa is filled with the high-purity argon gas of 0.4 ~ 0.6MPa into furnace, using water jacketed copper crucible suspension smelting furnace molten alloy
Ingot；
Step 4: 3 ~ 4 passage of molten alloy, obtains uniformly mixed alloy pig；
Step 5: carry out flat-die forging to alloy pig, 500 DEG C of initial forging temperature, 400 DEG C of final forging temperature, each deflection 20 ~
30%, total deformation is crushed coarse precipitated phase 60 ~ 70%, obtains uniform formation；
Step 6: forging stock is dissolved 12 hours at 540 DEG C ± 5 DEG C, in 25 DEG C of water of quenching；
Step 7: again 175 DEG C ± 5 timeliness 5 hours, it is air-cooled.
6. method as claimed in claim 5, which is characterized in that in second step, raw metal purity is greater than 99.5%.
7. method as claimed in claim 5, which is characterized in that the purity of high-purity argon gas is not less than 99.99%.
8. method as claimed in claim 5, which is characterized in that in the 4th step, monitor system 18-22KW.
9. method as claimed in claim 5, which is characterized in that there is 400 DEG C excellent of tensile strength of the material to reach
105 ~ 117MPa and elongation percentage 29% ~ 38%.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20210130934A1 (en) * | 2019-10-30 | 2021-05-06 | Sumit Bahl | Aluminum-cerium-copper alloys for metal additive manufacturing |
| CN114438383A (en) * | 2022-01-21 | 2022-05-06 | 常州工学院 | Multistage intermetallic compound reinforced heat-resistant alloy and preparation method thereof |
| CN115094277A (en) * | 2022-07-11 | 2022-09-23 | 上海交通大学 | Mixed crystal structure aluminum alloy and preparation method and application thereof |
| CN115323230A (en) * | 2022-07-29 | 2022-11-11 | 西安交通大学 | Aluminum-copper-cerium series heat-resistant aluminum alloy and preparation method thereof |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB596178A (en) * | 1945-07-24 | 1947-12-30 | Tennyson Fraser Bradbury | Aluminium base alloys |
| SU387018A1 (en) * | 1970-12-18 | 1973-06-21 | ALLOY BASED ON ALUMINUM | |
| CN101363092A (en) * | 2008-07-09 | 2009-02-11 | 贵州铝厂 | High-strength cast aluminium alloy material |
| CN102758109A (en) * | 2012-08-07 | 2012-10-31 | 曾琦 | High-strength wear-resisting heat-resisting aluminium alloy material and preparation process thereof |
| CN104313418A (en) * | 2014-11-07 | 2015-01-28 | 安徽瑞研新材料技术研究院有限公司 | High-performance heat-resistant aluminum alloy material |
| CN104372219A (en) * | 2013-08-16 | 2015-02-25 | 镇江忆诺唯记忆合金有限公司 | Method for increasing Al-Cu-Mn-Ti alloy thermal fatigue performance by adding Ce |
| RU2604084C1 (en) * | 2015-09-02 | 2016-12-10 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | Aluminium-based filler material, alloyed with rare-earth metals |
-
2019
- 2019-03-14 CN CN201910193124.9A patent/CN109797326B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB596178A (en) * | 1945-07-24 | 1947-12-30 | Tennyson Fraser Bradbury | Aluminium base alloys |
| SU387018A1 (en) * | 1970-12-18 | 1973-06-21 | ALLOY BASED ON ALUMINUM | |
| CN101363092A (en) * | 2008-07-09 | 2009-02-11 | 贵州铝厂 | High-strength cast aluminium alloy material |
| CN102758109A (en) * | 2012-08-07 | 2012-10-31 | 曾琦 | High-strength wear-resisting heat-resisting aluminium alloy material and preparation process thereof |
| CN104372219A (en) * | 2013-08-16 | 2015-02-25 | 镇江忆诺唯记忆合金有限公司 | Method for increasing Al-Cu-Mn-Ti alloy thermal fatigue performance by adding Ce |
| CN104313418A (en) * | 2014-11-07 | 2015-01-28 | 安徽瑞研新材料技术研究院有限公司 | High-performance heat-resistant aluminum alloy material |
| RU2604084C1 (en) * | 2015-09-02 | 2016-12-10 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | Aluminium-based filler material, alloyed with rare-earth metals |
Non-Patent Citations (3)
| Title |
|---|
| G.Y.AN等: "Effect of Ce on the interface stability and dendrite arm spacing of Al-Cu alloys", 《JOURNAL OF CRYSTAL GROWTH》 * |
| 李海等: "Al-Cu-Ce合金的微观组织与力学性能", 《材料热处理学报》 * |
| 肖于德等: "耐热铝合金及其热稳强化相", 《铝加工》 * |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20210130934A1 (en) * | 2019-10-30 | 2021-05-06 | Sumit Bahl | Aluminum-cerium-copper alloys for metal additive manufacturing |
| CN114438383A (en) * | 2022-01-21 | 2022-05-06 | 常州工学院 | Multistage intermetallic compound reinforced heat-resistant alloy and preparation method thereof |
| CN115094277A (en) * | 2022-07-11 | 2022-09-23 | 上海交通大学 | Mixed crystal structure aluminum alloy and preparation method and application thereof |
| CN115094277B (en) * | 2022-07-11 | 2023-01-24 | 上海交通大学 | Mixed crystal structure aluminum alloy and preparation method and application thereof |
| CN115323230A (en) * | 2022-07-29 | 2022-11-11 | 西安交通大学 | Aluminum-copper-cerium series heat-resistant aluminum alloy and preparation method thereof |
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