CN100567537C - Low-temperature in-site generates the preparation technology of TiC particle reinforced magnesium base compound material - Google Patents
Low-temperature in-site generates the preparation technology of TiC particle reinforced magnesium base compound material Download PDFInfo
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- CN100567537C CN100567537C CNB2008100166285A CN200810016628A CN100567537C CN 100567537 C CN100567537 C CN 100567537C CN B2008100166285 A CNB2008100166285 A CN B2008100166285A CN 200810016628 A CN200810016628 A CN 200810016628A CN 100567537 C CN100567537 C CN 100567537C
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Abstract
The present invention relates to a kind of magnesium base composite material, particularly a kind of low-temperature in-site generates the TiC ceramic particle and strengthens magnesium base composite material and preparation technology thereof.This matrix material is to be made by following raw materials by weight percent: Al:8～9%, and Zn:0.5～1%, Ti:1.6～8%, C:0.4～2%, Ce:0.05～0.1%, Mn:0.3～1%, all the other are no more than 0.1% unavoidable impurities for Mg and total amount.Its preparation technology is: the preparation of (1) Al-Ti-C-Ce prefabricated section; (2) secondary smelting.The present invention can significantly reduce the temperature of reaction in, increases resistance to deformation, improves mechanical behavior under high temperature, improves material at the normal temperature wear resisting property under the hot conditions particularly.
Description
Technical field
The present invention relates to a kind of magnesium base composite material, particularly a kind of low-temperature in-site generates the TiC ceramic particle and strengthens magnesium base composite material and preparation technology thereof.
Background technology
Magnuminium not only has abundant raw material, advantages of good casting and machinability, and it is compared its volume density and only 2/3 has higher specific tenacity and specific rigidity for aluminum base alloy with aluminum base alloy.At present, Magnuminium is being used widely aspect the auto-parts such as wheel box, clutch coupling, wheel hub as the substitute of part steel, aluminum.But problem such as magnesium alloy itself exists wears no resistance, creep resistance is poor, working temperature is low has limited the application of magnesium base alloy material greatly.At present, the working temperature of creep resistance Dow metal has only 150～170 ℃, and the working temperature of ordinary magnesium alloy has only 120 ℃.These problems have become the development bottleneck of magnesium alloy.
Studies show that, in magnesium alloy, add ceramic particle and prepare matrix material, can not only obviously improve room temperature strength and wear resisting property, but also can further improve the mechanical behavior under high temperature of material.Because outer addition causes the interface pollution of adding between particle and the matrix easily, so the in-situ endogenic method is the main technique for preparing particles reiforced metal-base composition at present.But the temperature general requirement of reaction in is higher, being reflected at more than 850 ℃ of Al-Ti-B system for example, and the temperature of reaction of Al-Ti-C system is at 750～800 ℃, and this causes the magnesium alloy substrate oxidation serious, becomes the bottleneck of magnesium base composite material development.
The present invention is by strengthening the composition design and the optimization of system to magnesium base composite material, significantly reduced the temperature of reaction in, and the improvement of passing through melting technology generates the tiny ceramic particle that disperse distributes in matrix, and with the matrix good binding, thereby form mechanical property, physicals and the good matrix material of friction and wear behavior.The synthetic ceramic particle plays the effect of wear-resisting particle in matrices of composite material, rely on the characteristics of himself high rigidity and high rigidity and to the pinning effect of alloy substrate, increase resistance to deformation, improve mechanical behavior under high temperature, improve material at the normal temperature wear resisting property under the hot conditions particularly.
Summary of the invention
The objective of the invention is to by magnesium base composite material being strengthened the composition design and the optimization of system, add the catalyzer of TiC ceramic particle, significantly reduced the temperature of reaction in, and the improvement of passing through melting technology generates the tiny ceramic particle that disperse distributes in matrix, and with the matrix good binding, thereby form mechanical property, physicals and the good matrix material of friction and wear behavior.The synthetic ceramic particle plays the effect of wear-resisting particle in matrices of composite material, rely on the characteristics of himself high rigidity and high rigidity and to the pinning effect of alloy substrate, increase resistance to deformation, improve mechanical behavior under high temperature, improve material at the normal temperature wear resisting property under the hot conditions particularly.
Another object of the present invention is to provide the preparation technology of above-mentioned matrix material.
The present invention realizes by following measure:
Low-temperature in-site of the present invention generates the TiC ceramic particle and strengthens magnesium base composite material, be to be made by following raw materials by weight percent: Al 8～9%, Zn 0.5～1%, Ti 1.6～8%, C0.4～2%, Ce 0.05～0.1%, and Mn 0.3～1%, and all the other are no more than 0.1% unavoidable impurities for Mg and total amount.
The optimum weight per-cent of described raw material is: Al 9%, and Zn 0.8%, and Ti 4%, and C 1%, and Ce 0.08%, and Mn 0.8%, and all the other are no more than 0.1% unavoidable impurities for Mg and total amount.
The present invention also provides the preparation technology of above-mentioned matrix material, adopts following steps:
(1) preparation of Al-Ti-C-Ce prefabricated section:
Take by weighing raw material by following weight percent: Al 30～49%, and Ti 40～56%, and C 10～14%, and Ce 0.5～1%; Raw material is mixed, dries, is pressed into prefabricated section, with prefabricated section be heated to 300～400 ℃ standby; Raw materials used: Al powder and the Ce content of the Ti powder of granularity≤75 μ m, the granularity≤amorphous C powder of 15 μ m, granularity≤75 μ m are the Al-Ce alloy powder of 10wt% granularity≤120 μ m;
(2) secondary smelting:
By the Al material after the aluminium amount of introducing in the composition proportion of matrix material and the deduction prefabricated section,, alloy liquid is warming up to 700～720 ℃ and be incubated 10～20min with magnesium material, aluminium material, zinc material, manganese material shove charge fusing; Adopt the bell jar plunging will be pressed into the liquation bottom, be cooled to 660～680 ℃ behind insulation 5～10min, stir alloy liquid 5-8min, reaction in is carried out thoroughly through the Al-Ti-C-Ce prefabricated section of preheating; After stir finishing alloy liquid is warmed up to once more 700～720 ℃ stir and leave standstill 2～4min after, skim casting.Alloy liquid adopts SF in melting or whipping process
6+ CO
2Gas is as shielding gas.Fusion process adopts temperature-rise period twice, is warming up to 700～720 ℃ of higher temperature of adding prefabricated section for the first time and helps carrying out smoothly of reaction in, is cooled to 660～680 ℃ then and stirs the oxidative phenomenas that liquations reduce alloys.Heat up 700～720 ℃ for the second time and skim, be cast with to be beneficial to and purify the matrix composition, make particles dispersed even simultaneously.
The present invention is the enhancing system with Al-Ti-C-Ce, adopts the method for prefabricated briquetting reaction in liquid magnesium alloy, has synthesized the TiC particle in metal melt.The adding of Ce element is played katalysis to TiC synthetic in the enhancing system, makes the reaction in temperature reduce by 50～80 ℃, and reaction in synthesize ceramic particle can carry out at a lower temperature smoothly, and matrix alloy is difficult for the oxidation burning in preparation process.Studies show that the Ce that adds 0.5wt%～1.0wt% in the Al-Ti-C system makes Ti and C reaction in temperature significantly reduce.Original position synthetic TiC particle fine size is at 1～3 μ m, be evenly distributed in matrix, and is good with the matrix wettability, the bonding strength height.
The Composite Preparation process adopts secondary smelting technology, can avoid the sedimentation in matrix material of TiC particle so that the TiC particle that generates is evenly distributed on the one hand in matrix, can make the reaction clout produce scum silica frost on the other hand, purifies matrix.This preparation melting technology is easy, and production cost is low.
It is that reaction in system+secondary smelting technology obtains matrix material that ceramic particle strengthens magnesium base composite material employing Al-Ti-C-Ce.By adjust the aluminium in the Al-Ti-C-Ce system, the content of Ce elements reduces the temperature of reaction in, makes the TiC even particle distribution that generates and purify matrix by secondary smelting technology.
The present invention is by strengthening the composition design and the optimization of system to magnesium base composite material, add the catalyzer of TiC ceramic particle, significantly reduced the temperature of reaction in, and the improvement of passing through melting technology generates the tiny ceramic particle that disperse distributes in matrix, and with the matrix good binding, thereby form mechanical property, physicals and the good matrix material of friction and wear behavior.The synthetic ceramic particle plays the effect of wear-resisting particle in matrices of composite material, rely on the characteristics of himself high rigidity and high rigidity and to the pinning effect of alloy substrate, increase resistance to deformation, improve mechanical behavior under high temperature, improve material at the normal temperature wear resisting property under the hot conditions particularly.
Material of the present invention strengthens the composition proportion of system and adopts secondary smelting technology by design and optimization original position, makes material of the present invention obtain good performance.With the AZ91 alloy ratio, especially the wear resistance of material, hardness tensile strength and modulus are greatly improved, made have high strength, high-wearing feature and better the ceramic particle of high-temperature behavior strengthen magnesium base composite material.
Embodiment
Embodiment 1
With the composition proportion production standard tensile test piece of material shown in the table 11, adopt the resistance furnace melting to make material.
Choose the Al-Ti-C-Ce prefabricated section according to the preparation technology of prefabricated section and account for matrix material weight percent 8.33%.Wherein Al powder (granularity≤75 μ m) accounts for 32wt% in the prefabricated section, and Ti powder (granularity≤75 μ m) accounts for 48wt%, and C powder (granularity≤15 μ m) accounts for 12wt%, and Al-0.1Ce powder (granularity≤120 μ m) accounts for 8wt%.Powder is mixed, be pressed into the prefabricated block of diameter 30mm, height 20mm.According to composite material compositions design, material such as magnesium, zinc are melted be warming up to 720 ℃ and be incubated 15min.The Al-Ti-C-Ce prefabricated section that adopts the bell jar plunging will be preheating to 350 ℃ is pressed into the liquation bottom, is cooled to 670 ℃ behind the insulation 8min, stirs alloy liquid 5min.After stir finishing alloy liquid is warmed up to once more 720 ℃ stir and leave standstill 3min after, skim casting.
The chemical ingredients (wt%) of the material of the present invention that table 1 is implemented
The average tensile strength of material 1 sample (σ b) reaches 220MPa, and hardness reaches 68HB, and modulus (E) reaches 47Gpa, and linear expansivity is 24.55 * 10
-6(20-150 ℃).With the AZ91 alloy ratio, the tensile strength of this matrix material, hardness, modulus have improved 15%, 34% and 11.9% respectively, wear rate has reduced 75%, linear expansivity has reduced 5.5%.
Embodiment 2
With the composition proportion production standard tensile test piece of material shown in the table 12, adopt the resistance furnace melting to make material.
Choosing the Al-Ti-C-Ce prefabricated section according to the preparation technology of prefabricated section, to account for the matrix material weight percent be 5%.Wherein Al powder (granularity≤75 μ m) accounts for 30wt% in the prefabricated section, and Ti powder (granularity≤75 μ m) accounts for 48wt%, and C powder (granularity≤15 μ m) accounts for 12wt%, Al-0.1Ce powder] (granularity≤120 μ m) account for 10wt%.Powder is mixed, be pressed into the prefabricated block of diameter 30mm, height 20mm.According to composite material compositions design, material such as magnesium, zinc are melted be warming up to 710 ℃ and be incubated 15min.The Al-Ti-C-Ce prefabricated section that adopts the bell jar plunging will be preheating to 330 ℃ is pressed into the liquation bottom, is cooled to 670 ℃ behind the insulation 7min, stirs alloy liquid 5min.After stir finishing alloy liquid is warmed up to once more 710 ℃ stir and leave standstill 3min after, skim casting.
The average tensile strength of material 2 samples (σ b) reaches 211MPa, and hardness reaches 60HB, and modulus (E) reaches 45.2GPa, and linear expansivity is 24.91 * 10
-6(20-150 ℃).With the AZ91 alloy ratio, the tensile strength of this matrix material, hardness, modulus have improved 10.2%, 18.3% and 7.6% respectively, wear rate has reduced 50%, linear expansivity has reduced 3.9%.
Claims (2)
1. a low-temperature in-site generates the preparation technology that the TiC ceramic particle strengthens magnesium base composite material, it is characterized in that adopting following steps:
(1) preparation of Al-Ti-C-Ce prefabricated section:
Take by weighing raw material by following weight percent: Al 30～49%, and Ti 40～56%, and C 10～14%, and Ce 0.5～1%; Raw material is mixed, dries, is pressed into prefabricated section, with prefabricated section be heated to 300～400 ℃ standby; Raw materials used: Al powder and the Ce content of the Ti powder of granularity≤75 μ m, the granularity≤amorphous C powder of 15 μ m, granularity≤75 μ m are the Al-Ce alloy powder of 10wt% granularity≤120 μ m;
(2) secondary smelting:
By the Al material after the aluminium amount of introducing in the composition proportion of matrix material and the deduction prefabricated section,, alloy liquid is warming up to 700～720 ℃ and be incubated 10～20min with magnesium material, aluminium material, zinc material, manganese material shove charge fusing; Adopt the bell jar plunging will be pressed into the liquation bottom, be cooled to 660～680 ℃ behind insulation 5～10min, stir alloy liquid 5-8min, reaction in is carried out thoroughly through the Al-Ti-C-Ce prefabricated section of preheating; After stir finishing alloy liquid is warmed up to once more 700～720 ℃ stir and leave standstill 2～4min after, skim casting;
(3) described matrix material is to be made by following raw materials by weight percent: Al 8～9%, and Zn 0.5～1%, and Ti 1.6～8%, C 0.4～2%, Ce 0.05～0.1%, and Mn 0.3～1%, and all the other are no more than 0.1% unavoidable impurities for Mg and total amount.
2. preparation technology according to claim 1 is characterized in that: alloy liquid adopts SF in melting or whipping process
6+ CO
2Gas is as shielding gas.
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| CN104313431A (en) * | 2014-10-24 | 2015-01-28 | 俞虹 | Preparation method of self-lubricating damping alloy |
| CN104313367A (en) * | 2014-10-24 | 2015-01-28 | 俞虹 | Preparation method of self-lubricating wear-resistant and vibration-absorptive alloy |
| CN104313430A (en) * | 2014-10-24 | 2015-01-28 | 严静儿 | Wear-resistant damping alloy and preparation method thereof |
| CN104313428A (en) * | 2014-10-24 | 2015-01-28 | 严静儿 | Self-lubricating wear-resistant damping alloy and preparation method thereof |
| CN104313435A (en) * | 2014-10-24 | 2015-01-28 | 陈唯锋 | Preparation method of wear resistant alloy material |
| CN104313429A (en) * | 2014-10-24 | 2015-01-28 | 严静儿 | Wearing-resisting damping alloy preparation method |
| CN105603240B (en) * | 2016-01-21 | 2017-08-22 | 大连理工大学 | A kind of use Al Ti X self- propagatings system prepares the method without magnalium based composites |
| CN108149241A (en) * | 2017-12-01 | 2018-06-12 | 重庆文理学院 | A kind of laser cladding strengthens the preparation method of cutter |
-
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Non-Patent Citations (6)
| Title |
|---|
| In situ synthesis method and damping characterizationof magnesium matrix composites. Zhang Xiuqing et al.Composites science and technology. 2007 |
| In situ synthesis method and damping characterizationof magnesium matrix composites. Zhang Xiuqing et al.Composites science and technology. 2007 * |
| TiC/AZ91复合材料微观断裂机制的研究. 王彬等.铸造，第56卷第10期. 2007 |
| TiC/AZ91复合材料微观断裂机制的研究. 王彬等.铸造，第56卷第10期. 2007 * |
| 变形镁及镁合金牌号和化学成分 GB/T 5153-2003. 吴欣凤等，1-3，国家质量监督检验检疫总局. 2003 |
| 变形镁及镁合金牌号和化学成分 GB/T 5153-2003. 吴欣凤等，1-3，国家质量监督检验检疫总局. 2003 * |
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