CN108085528B - In-situ generated nano NbB2Method for grain refining and strengthening aluminum alloy - Google Patents

In-situ generated nano NbB2Method for grain refining and strengthening aluminum alloy Download PDF

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CN108085528B
CN108085528B CN201711274134.2A CN201711274134A CN108085528B CN 108085528 B CN108085528 B CN 108085528B CN 201711274134 A CN201711274134 A CN 201711274134A CN 108085528 B CN108085528 B CN 108085528B
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powder
nbb
aluminum alloy
aluminum
alloy
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CN108085528A (en
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邱丰
李强
常芳
姜启川
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Jilin University
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Abstract

The invention relates to an in-situ nano NbB2The method for refining and strengthening the aluminum alloy by the particles specifically comprises the following four steps of (1) in-situ generating nanometer NbB2Particle refinement and preparation of an enhancer; (2) preparing an aluminum alloy subjected to unrefined and strengthened treatment; (3) endogenous nano NbB2Strengthening treatment of the aluminum alloy by ceramic particles; the technical method has high refining and strengthening efficiency, is simple and convenient to operate, and is particularly suitable for structure refining and performance strengthening of high-silicon-content aluminum alloy. After the aluminum alloy is refined and strengthened, alpha-Al dendrite is obviously refined, and the mechanical property of the alloy is obviously improved: the yield strength, the tensile strength and the plasticity are obviously improved; small amount of nano NbB2The addition of the particles can achieve a better effect, the application field of the refined and strengthened aluminum alloy is further expanded, a new solution is provided for the thin-wall light weight of the aluminum alloy, and the method has important practical application value.

Description

In-situ generated nano NbB2Method for grain refining and strengthening aluminum alloy
Technical Field
The invention relates to the field of aluminum alloy processing and preparation, in particular to in-situ nano NbB2A method for grain refining and strengthening aluminum alloy.
Background
In consideration of reducing energy consumption and environmental pollution, the reduction of the weight of the structural member and the mechanical properties of the reinforcing material promote the development of industries such as automobiles, aerospace and the like to light weight, wherein the aluminum alloy plays a key role. The aluminum alloy is easy to form, low in density, high in specific strength and corrosion resistantThe material with better corrosion performance is widely applied to manufacturing parts required in the transportation industry. In recent years, researchers have considered how to further improve the physical, chemical, mechanical, and other properties of aluminum alloy materials. As is well known, grain refinement is the key to improving the mechanical properties of materials, and grain refinement and material strengthening are usually achieved by adding a refiner containing ceramic particles and a strengthening agent. NbB2As a transition metal boride, the boron nitride has the excellent characteristics of high melting point, high hardness, good corrosion resistance, good high-temperature mechanical properties and the like. NbB2The niobium-silicon compound belongs to a high-temperature intermetallic compound, has high melting point and good chemical stability. The experimental result shows that Si is in AlNb3And AlNb2Medium solid solubility is low, in Al3The solid solubility in Nb is only 2 at.%. The possibility of forming niobium-silicon compounds in the aluminum melt at 800 ℃ is low, and therefore, the Nb-containing phase can be used as a heterogeneous nucleating agent for refining aluminum-silicon alloys without generating the poisoning effect of Si. In addition, the NbB with small size and large number2The nano-particles can be used as a substrate for alpha-Al heterogeneous nucleation to promote the alpha-Al heterogeneous nucleation. The non-nucleated nanoparticles can be adsorbed on a solid-liquid interface at the front end of dendritic crystal growth to form a nanoparticle layer, so that solute atoms are prevented from being transferred to the solidification front of the solid-liquid interface, the growth of the dendritic crystal is prevented, and the grains of the aluminum alloy are obviously refined. In situ endogenous NbB2The nano particles are uniformly dispersed in the aluminum alloy matrix, the agglomeration is less, the nano particles strengthen the aluminum alloy through fine grain strengthening, olowaten strengthening, pinning grain boundary, heat mismatching strengthening and the like, and the yield strength, tensile strength and plasticity of the whole material are obviously improved. To sum up, in situ generated NbB2The nano particles as a refining and strengthening agent of the aluminum alloy can be used for refining and strengthening the aluminum alloy, particularly for high-silicon aluminum alloy, and have important functions of improving the room temperature and high temperature performance of the aluminum alloy material, and resisting impact load, fatigue, creep and the like. The application field of the strengthened aluminum alloy is further expanded, the method has higher practical application value, simple operation and little in-situ endogenesisNbB2The application of the nano particles can obtain better strengthening effect, and provides an important solution idea and way for the thin wall and light weight of the aluminum alloy.
Disclosure of Invention
The invention aims to provide in-situ endogenous nanometer NbB2A method for grain refining and strengthening aluminum alloy.
The purpose of the invention can be realized by the following technical scheme:
in-situ generated nano NbB2The method for grain refining and strengthening the aluminum alloy comprises the following steps:
(1) in-situ nano NbB2Particle refinement and preparation of a reinforcing agent:
(1a) b, ball milling activation pretreatment of boron powder: putting boron powder into a ball milling tank, and carrying out ball milling activation treatment on the boron powder for 1-3 h at the speed of 200-300 r/min by using a ball mill;
(1b) preparing powder used for a reaction pressed compact: weighing aluminum powder with the required particle size of 13-48 mu m, and performing ball milling treatment on boron powder with the particle size of 0.5-1 mu m, niobium powder with the particle size of 48 mu m and copper powder with the particle size of 45 mu m for later use; preparing 100g of mixed powder from aluminum powder, niobium powder, boron powder and copper powder according to the following mixture ratio to prepare an Al-Nb-B-Cu green compact; wherein the mass ratio of Nb to B is 4.30:1 respectively, and the molar ratio is 1: 2; wherein the content of the aluminum powder is 60-90 wt.%; the content of niobium powder is 8.11-32.45 wt.%; the content of boron powder is 1.89-7.55 wt.%; the content of the Cu powder is 0-5 wt.%, and the specific content is as follows:
firstly, reacting in Al-Nb-B system to generate nano NbB2The mass fraction of ceramic particles was 10 wt.%; the aluminum powder, the niobium powder, the boron powder and the copper powder in the system respectively have the following weight: aluminum powder: 90 g; niobium powder: 8.11 g; boron powder: 1.89 g; copper powder: 0 g; preparing 100g of mixed powder; wherein, the nanometer NbB2The Nb/B mass ratio in the ceramic particles is 4.30: 1; the Nb/B molar ratio is 1: 2;
② the nano NbB is generated by the reaction in the Al-Nb-B system2Mass fraction of ceramic particles 20 wt.%; the aluminum powder, the niobium powder, the boron powder and the copper powder in the system respectively have the following weight: aluminum powder: 80 g; niobium powder: 16.22 g; boron powder: 3.78 g; copper powder:0 g; preparing 100g of mixed powder; wherein, the nanometer NbB2The Nb/B mass ratio in the ceramic particles is 4.30: 1; the Nb/B molar ratio is 1: 2;
③ reaction in Al-Nb-B system to generate nanometer NbB2Mass fraction of ceramic particles 30 wt.%; the aluminum powder, the niobium powder, the boron powder and the copper powder in the system respectively have the following weight: aluminum powder: 70 g; niobium powder: 24.33 g; boron powder: 5.67 g; copper powder: 0 g; preparing 100g of mixed powder; wherein, the nanometer NbB2The Nb/B mass ratio in the ceramic particles is 4.30: 1; the Nb/B molar ratio is 1: 2;
reacting in Al-Nb-B system to generate nano NbB2Mass fraction of ceramic particles 40 wt.%; the aluminum powder, the niobium powder, the boron powder and the copper powder in the system respectively have the following weight: aluminum powder: 60 g; niobium powder: 32.45 g; boron powder: 7.55 g; copper powder: 0 g; preparing 100g of mixed powder; wherein, the nanometer NbB2The Nb/B mass ratio in the ceramic particles is 4.30: 1; the Nb/B molar ratio is 1: 2;
reacting in Al-Nb-B-Cu system to generate NbB2The mass fraction of the ceramic particles was 30 wt.%, wherein the content of Cu element was 5 wt.%; the aluminum powder, the niobium powder, the boron powder and the copper powder in the system respectively have the following weight: aluminum powder: 65 g; niobium powder: 24.33 g; boron powder: 5.67 g; copper powder: 5 g; preparing 100g of mixed powder; wherein, the nanometer NbB2The Nb/B mass ratio in the ceramic particles is 4.30: 1; the Nb/B molar ratio is 1: 2;
(1c) ball-milling and mixing the powder used for the reaction pressed compact: putting the prepared mixed powder with different components and zirconia grinding balls into a mixer, and filling ZrO with diameters of 5mm, 7mm, 11mm, 15mm, 20mm and 22mm into a tank 210 balls each of ZrO2The ball mass is 800 g; uniformly mixing for 8-32 h at the speed of 30-60 r/min by using a mixer; wherein the mass ratio of the zirconia grinding ball to the mixed powder is 8: 1;
(1d) preparation of reaction green compacts: taking out the powder of the ball-milling mixed material, wrapping the powder of the ball-milling mixed material with an aluminum foil, and performing cold pressing on the wrapped powder on a hydraulic press to obtain a phi 30 cylindrical pressed blank with the height of 35-45 mm; the density is 60-75%;
(1e) in-situ reaction of nanoparticles:
wrapping the phi 30 cylindrical pressed blank prepared in the step (2) by graphite paper, and putting the wrapped pressed blank into a graphite mold;
secondly, putting the graphite mould and the phi 30 cylindrical pressed blank into a vacuum thermal explosion furnace, closing a furnace door, and vacuumizing until the pressure in the furnace is lower than 10 Pa;
beginning to heat, and setting the heating speed to be 25-40K/min; heating to 1183K, then reducing the temperature to 1073K, preserving the heat for 10min, and applying axial pressure of 25-55 MPa to the cylindrical pressed compact in the heat preservation process for 20-60 s; cooling the cylindrical ceramic-aluminum composite furnace which is densified by axial pressure to room temperature in vacuum after reaction;
(2) preparation of unrefined and strengthened aluminum alloy:
(2a) placing the pre-weighed aluminum alloy into a crucible, placing the crucible and the aluminum alloy into a crucible type resistance smelting furnace, and heating to 1023K; the aluminum alloy comprises the following components: Al-Si7-Mn0.65-Mg0.33、Al-Si10-Cu-Mg0.39；
(2b) After the alloy is completely melted, preserving heat for 30min, adding 0.05-0.10 wt.% of slag removing agent to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3) endogenous nano NbB2Strengthening treatment of the ceramic particles on the aluminum alloy:
(3a) after the weighed alloy is put into a crucible and is put into a furnace together with the crucible, the temperature is increased to 1123K;
(3b) after the alloy is completely melted, preserving heat for 30min, adding 0.05-0.10 wt.% of slag removing agent to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3c) will contain NbB2Adding ceramic particle reinforcer into the alloy liquid, NbB2The actual adding amount of the ceramic particles is 0.1-0.3 wt%, and the mixed alloy liquid is subjected to ultrasonic treatment for 3-10 min; NbB2The Nb/B mass ratio in the ceramic particles is 4.30: 1; the Nb/B molar ratio is 1: 2;
(3d) casting the metal liquid after ultrasonic treatment into a metal mold, solidifying and cooling to obtain the nano-scale NbB2Plate-like patterns of refined and strengthened aluminum alloy of ceramic particles.
Preferably, the metal mold in step (3d) is made of: 45# steel, the size of the metal mold is as follows: 200mm by 150mm by 20 mm.
The microstructure and the mechanical property of the material are obviously optimized: under the conditions of optimal refinement and strengthening (NbB in Al-7Si-0.65Mn-0.33Mg alloy)2The addition amount of the ceramic particles is 0.1 wt.%, and Nb/B is 1:2), the crystal grains of the aluminum alloy are obviously refined, and the yield strength, the tensile strength and the breaking strain of the alloy in an as-cast state are respectively 168.7MPa, 255.2MPa and 8.6 percent. The yield strength, tensile strength and breaking strain of the aluminum alloy without thinning and strengthening treatment in an as-cast state are 143.9MPa, 205.0MPa and 6.0 percent respectively. By adding NbB2After the aluminum alloy is refined and strengthened by the nano particles, the yield strength, the tensile strength and the fracture strain of the alloy are respectively improved by 17.2 percent, 24.5 percent and 43.3 percent compared with the untreated alloy, and the mechanical property is obviously improved.
The invention has the beneficial effects that: in-situ generated nano NbB in the invention2The method for refining and strengthening the aluminum alloy by the particles specifically comprises the following four steps of (1) in-situ generating nanometer NbB2Particle refinement and preparation of an enhancer; (2) preparing an aluminum alloy subjected to unrefined and strengthened treatment; (3) endogenous nano NbB2Strengthening treatment of the aluminum alloy by ceramic particles; the technical method has high refining and strengthening efficiency, is simple and convenient to operate, and is particularly suitable for structure refining and performance strengthening of high-silicon-content aluminum alloy. After the aluminum alloy is refined and strengthened, alpha-Al dendrite is obviously refined, and the mechanical property of the alloy is obviously improved: the yield strength, the tensile strength and the plasticity are obviously improved; small amount of nano NbB2The addition of the particles can achieve a better effect, the application field of the refined and strengthened aluminum alloy is further expanded, a new solution is provided for the thin-wall light weight of the aluminum alloy, and the method has important practical application value.
Drawings
FIG. 1 shows Al-Si without fining and strengthening treatment7-Mn0.65-Mg0.33An as-cast grain structure diagram of an aluminum alloy.
FIG. 2 shows Al-Si without refinement and strengthening10-Cu-Mg0.39An as-cast grain structure diagram of an aluminum alloy.
FIG. 3 is the addition of 0.1 wt.% NbB in example 12Al-Si of ceramic particles7-Mn0.65-Mg0.33As-cast grain structure diagram of the alloy.
FIG. 4 is the addition of 0.1 wt.% NbB in example 12Al-Si of ceramic particles7-Mn0.65-Mg0.33Tensile stress strain curve of the alloy as cast.
FIG. 5 is the addition of 0.1 wt.% NbB in example 22Al-Si of ceramic particles7-Mn0.65-Mg0.33As-cast grain structure diagram of the alloy.
FIG. 6 is the addition of 0.1 wt.% NbB in example 22Al-Si of ceramic particles7-Mn0.65-Mg0.33Tensile stress strain curve of the alloy as cast.
FIG. 7 is the addition of 0.3 wt.% NbB in example 32Al-Si of ceramic particles7-Mn0.65-Mg0.33As-cast grain structure diagram of the alloy.
FIG. 8 is the addition of 0.3 wt.% NbB in example 32Al-Si of ceramic particles7-Mn0.65-Mg0.33Tensile stress strain curve of the alloy as cast.
FIG. 9 is the addition of 0.3 wt.% NbB in example 42Al-Si of ceramic particles7-Mn0.65-Mg0.33As-cast grain structure diagram of the alloy.
FIG. 10 is the addition of 0.3 wt.% NbB in example 42Al-Si of ceramic particles7-Mn0.65-Mg0.33Tensile stress strain curve of the alloy as cast.
FIG. 11 is the addition of 0.3 wt.% NbB in example 52Al-Si of ceramic particles10-Cu-Mg0.39As-cast grain structure diagram of the alloy.
FIG. 12 is the addition of 0.3 wt.% NbB in example 52Al-Si of ceramic particles10-Cu-Mg0.39Tensile stress strain curve of the alloy as cast.
Detailed Description
In order to make the technical means, innovative features and attainments objectives easier to understand, the invention will be further described with reference to the following embodiments.
Example 1:
in-situ generated nano NbB in the embodiment2The method for grain refining and strengthening the aluminum alloy comprises the following steps:
(1) in-situ nano NbB2Particle refinement and preparation of a reinforcing agent:
(1a) b, ball milling activation pretreatment of boron powder: putting boron powder into a ball milling tank, and carrying out ball milling activation treatment on the boron powder for 3 hours at the speed of 200r/min by using a ball mill;
(1b) preparing powder used for a reaction pressed compact: weighing a certain amount of aluminum powder with the required granularity of 25 mu m, and carrying out ball milling treatment on boron powder with the granularity of 0.5 mu m and niobium powder with the granularity of 48 mu m for later use. The Al-Nb-B green compact is prepared by preparing 100g of mixed powder from aluminum powder, niobium powder and boron powder according to the following mixture ratio. Wherein the Al-Nb-B system reacts to generate nano NbB2The mass fraction of ceramic particles (Nb/B mass ratio 4.30: 1; Nb/B molar ratio 1:2) was 10 wt.%: the aluminum powder, the niobium powder and the boron powder in the system respectively have the following weight: aluminum powder: 90 g; niobium powder: 8.11 g; boron powder: 1.89 g; preparing 100g of mixed powder;
(1c) ball-milling and mixing the powder used for the reaction pressed compact: putting the prepared mixed powder with different components and zirconia grinding balls into a mixer, and filling ZrO with diameters of 5mm, 7mm, 11mm, 15mm, 20mm and 22mm into a tank 210 balls each of ZrO2The total ball mass is 800 g. Uniformly mixing for 32 hours at the speed of 30r/min by using a mixer; wherein the mass ratio of the zirconia grinding ball to the mixed powder is 8: 1;
(1d) preparation of reaction green compacts: taking out the powder of the ball-milling mixed material, wrapping the powder of the ball-milling mixed material with an aluminum foil, and performing cold pressing on the wrapped powder on a hydraulic press to obtain a phi 30 cylindrical pressed blank with the height of 40 mm; the density is 70%;
(1e) in-situ reaction of nanoparticles:
wrapping the phi 30 cylindrical pressed blank prepared in the step (2) by graphite paper, and putting the wrapped pressed blank into a graphite mold;
secondly, putting the graphite mould and the phi 30 cylindrical pressed blank into a vacuum thermal explosion furnace, closing a furnace door, and vacuumizing until the pressure in the furnace is lower than 10 Pa;
beginning to heat, and setting the heating speed to be 35K/min; heating to 1183K, then reducing the temperature to 1073K, preserving the heat for 10min, and simultaneously applying axial pressure of 45MPa to the cylindrical pressed compact in the heat preservation process for 25 s; cooling the cylindrical ceramic-aluminum composite furnace which is densified by axial pressure to room temperature in vacuum after reaction;
(2) preparation of unrefined and strengthened aluminum alloy:
(2a) placing the pre-weighed aluminum alloy into a crucible, placing the crucible and the aluminum alloy into a crucible type resistance smelting furnace, and heating to 1023K; the aluminum alloy comprises the following components: Al-Si7-Mn0.65-Mg0.33；
(2b) After the alloy is completely melted, preserving heat for 30min, adding 0.05 wt.% of slag removing agent to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3) step three, generating the nano NbB2Strengthening treatment of the ceramic particles on the aluminum alloy:
(3a) after the weighed alloy is put into a crucible and is put into a furnace together with the crucible, the temperature is increased to 1123K;
(3b) after the alloy is completely melted, preserving heat for 30min, adding 0.05 wt.% of slag removing agent to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3c) will contain NbB2Adding ceramic particle reinforcer into the alloy liquid, NbB2The actual addition of ceramic particles was 0.1 wt.% (Nb/B mass ratio 4.30: 1; Nb/B molar ratio 1:2), and the mixed alloy liquid was subjected to ultrasonic treatment for 3 min;
(3d) casting the metal liquid after ultrasonic treatment into a metal mold, solidifying and cooling to obtain the nano NbB2Plate-like patterns of refined and strengthened aluminum alloy of ceramic particles.
Wherein, the metal mold in the step (3d) is made of the following materials: 45# steel, the size of the metal mold is as follows: 200mm by 150mm by 20 mm.
In-situ nano NbB2The ceramic particles can be used as an effective refining and strengthening agent of the aluminum alloy. FIG. 3 shows a structure in which Al-Si is present7-Mn0.65-Mg0.33NbB in alloy2As-cast grain structure diagram with ceramic particles added in an amount of 0.1 wt.%. Compared with the aluminum alloy structure without the thinning treatment (as shown in figure 1), the aluminum alloy crystal grains added with the nano particles are thinned. FIG. 4 is an addition of 0.1 wt.% NbB2Al-Si of ceramic particles7-Mn0.65-Mg0.33Tensile stress strain curve of the alloy as cast. Addition of NbB2Yield strength sigma of as-cast aluminum alloy after nanoparticles0.2163.2MPa for (MPa), 238.0MPa for UTS (MPa) for tensile strength and ε for breaking strainf(%) was 8.8%. Compared with the tensile property of the aluminum alloy without thinning and strengthening treatment (yield strength: 143.9MPa, tensile strength: 205.0MPa, breaking strain: 6.0 percent), NbB is added2The yield strength, tensile strength and breaking strain of the aluminum alloy of the nano particles are respectively improved by 13.4%, 16.1% and 46.7%, and the mechanical property is obviously improved, as shown in figure 4 and table 1.
Example 2:
in-situ generated nano NbB in the embodiment2The method for grain refining and strengthening the aluminum alloy comprises the following steps:
(1) in-situ nano NbB2Particle refinement and preparation of a reinforcing agent:
(1a) b, ball milling activation pretreatment of boron powder: putting boron powder into a ball milling tank, and carrying out ball milling activation treatment on the boron powder for 3 hours at the speed of 200r/min by using a ball mill;
(1b) preparing powder used for a reaction pressed compact: weighing a certain amount of aluminum powder with the required granularity of 13 mu m, carrying out ball milling treatment on boron powder with the granularity of 0.5 mu m and niobium powder with the granularity of 48 mu m for later use; the Al-Nb-B green compact is prepared by preparing 100g of mixed powder from aluminum powder, niobium powder and boron powder according to the following mixture ratio. Wherein the Al-Nb-B system reacts to generate nano NbB2Mass fraction of ceramic particles (Nb/B mass ratio 4.30: 1; Nb/B molar ratio 1:2) 20 wt.%: system ofThe weight of the medium aluminum powder, the niobium powder and the boron powder is respectively as follows: aluminum powder: 80 g; niobium powder: 16.22 g; boron powder: 3.78 g; 100g of a mixed powder was prepared.
(1c) Ball-milling and mixing the powder used for the reaction pressed compact: putting the prepared mixed powder with different components and zirconia grinding balls into a mixer, and filling ZrO with diameters of 5mm, 7mm, 11mm, 15mm, 20mm and 22mm into a tank 210 balls each of ZrO2The total ball mass is 800 g. Uniformly mixing for 8 hours at the speed of 60r/min by using a mixer; wherein the mass ratio of the zirconia grinding ball to the mixed powder is 8: 1;
(1d) preparation of reaction green compacts:
taking out the powder of the ball-milling mixed material, wrapping the powder of the ball-milling mixed material with an aluminum foil, and performing cold pressing on the wrapped powder on a hydraulic press to obtain a phi 30 cylindrical pressed blank with the height of 35 mm; the density is 75%;
(1e) in-situ reaction of nanoparticles:
wrapping the phi 30 cylindrical pressed blank prepared in the step (2) by graphite paper, and putting the wrapped pressed blank into a graphite mold;
secondly, putting the graphite mould and the phi 30 cylindrical pressed blank into a vacuum thermal explosion furnace, closing a furnace door, and vacuumizing until the pressure in the furnace is lower than 10 Pa;
beginning to heat, and setting the heating speed to be 25K/min; heating to 1183K, then reducing the temperature to 1073K, preserving the heat for 10min, and simultaneously applying axial 55MPa pressure to the cylindrical pressed compact in the heat preservation process for 20 s; cooling the cylindrical ceramic-aluminum composite furnace which is densified by axial pressure to room temperature in vacuum after reaction;
(2) preparation of unrefined and strengthened aluminum alloy:
(2a) placing the pre-weighed aluminum alloy into a crucible, placing the crucible and the aluminum alloy into a crucible type resistance smelting furnace, and heating to 1023K; the aluminum alloy comprises the following components: Al-Si7-Mn0.65-Mg0.33；
(2b) After the alloy is completely melted, preserving heat for 30min, adding 0.10 wt.% slag remover to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3) endogenous nano NbB2Strengthening treatment of the ceramic particles on the aluminum alloy:
(3a) after the weighed alloy is put into a crucible and is put into a furnace together with the crucible, the temperature is increased to 1123K;
(3b) after the alloy is completely melted, preserving heat for 30min, adding 0.10 wt.% slag remover to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3c) will contain NbB2Adding ceramic particle reinforcer into the alloy liquid, NbB2The actual addition of ceramic particles was 0.1 wt.% (Nb/B mass ratio 4.30: 1; Nb/B molar ratio 1:2), and the mixed alloy liquid was subjected to ultrasonic treatment for 5 min;
(3d) casting the metal liquid after ultrasonic treatment into a metal mold, solidifying and cooling to obtain the nano NbB2Plate-like patterns of refined and strengthened aluminum alloy of ceramic particles.
Wherein, the metal mold in the step (3d) is made of the following materials: 45# steel, the size of the metal mold is as follows: 200mm by 150mm by 20 mm.
In-situ nano NbB2The ceramic particles can be used as an effective refining and strengthening agent of the aluminum alloy. FIG. 5 shows a structure in which Al-Si is present7-Mn0.65-Mg0.33NbB in alloy2As-cast grain structure diagram with ceramic particles added in an amount of 0.1 wt.%. Compared with the aluminum alloy structure without the thinning treatment (as shown in figure 1), the aluminum alloy crystal grains added with the nano particles are thinned. FIG. 6 is an addition of 0.1 wt.% NbB2Al-Si of ceramic particles7-Mn0.65-Mg0.33Tensile stress strain curve of the alloy as cast. Addition of NbB2Yield strength sigma of as-cast aluminum alloy after nanoparticles0.2(MPa) 168.7MPa, tensile strength UTS (MPa) 255.2MPa, strain at break εf(%) was 8.6%. Compared with the tensile property of the aluminum alloy without thinning and strengthening treatment (yield strength: 143.9MPa, tensile strength: 205.0MPa, breaking strain: 6.0 percent), NbB is added2The yield strength, tensile strength and breaking strain of the aluminum alloy of the nano particles are respectively improved by 17.2%, 24.5% and 43.3%, and the mechanical property is obviously improved, as shown in fig. 6 and table 1.
Example 3:
in-situ generated nano NbB in the embodiment2The method for grain refining and strengthening the aluminum alloy comprises the following steps:
(1) in-situ nano NbB2Particle refinement and preparation of a reinforcing agent:
(1a) b, ball milling activation pretreatment of boron powder: putting boron powder into a ball milling tank, and carrying out ball milling activation treatment on the boron powder for 3 hours at the speed of 200r/min by using a ball mill;
(1b) preparing powder used for a reaction pressed compact: weighing a certain amount of aluminum powder with the required granularity of 25 mu m, and performing ball milling treatment on boron powder with the granularity of 0.5 mu m, niobium powder with the granularity of 48 mu m and copper powder with the granularity of 48 mu m for later use; the Al-Nb-B-Cu green compact is prepared by preparing 100g of mixed powder from aluminum powder, niobium powder, boron powder and copper powder according to the following mixture ratio. Wherein the Al-Nb-B-Cu system reacts to generate nano NbB2The mass fraction of the ceramic particles (Nb/B mass ratio 4.30: 1; Nb/B molar ratio 1:2) was 30 wt.%, wherein the content of Cu element was 5 wt.%: the aluminum powder, the niobium powder, the boron powder and the copper powder in the system respectively have the following weight: aluminum powder: 65 g; niobium powder: 24.33 g; boron powder: 5.67 g; copper powder: 5 g; preparing 100g of mixed powder;
(1c) ball-milling and mixing the powder used for the reaction pressed compact: putting the prepared mixed powder with different components and zirconia grinding balls into a mixer, and filling ZrO with diameters of 5mm, 7mm, 11mm, 15mm, 20mm and 22mm into a tank 210 balls each of ZrO2The total ball mass is 800 g. Uniformly mixing for 20 hours at the speed of 45r/min by using a mixer; wherein the mass ratio of the zirconia grinding ball to the mixed powder is 8: 1;
(1d) preparation of reaction green compacts: taking out the powder of the ball-milling mixed material, wrapping the powder of the ball-milling mixed material with an aluminum foil, and performing cold pressing on the wrapped powder on a hydraulic press to obtain a phi 30 cylindrical pressed blank with the height of 35 mm; the density is 75%;
(1e) in-situ reaction of nanoparticles:
wrapping the phi 30 cylindrical pressed blank prepared in the step (2) by graphite paper, and putting the wrapped pressed blank into a graphite mold;
secondly, putting the graphite mould and the phi 30 cylindrical pressed blank into a vacuum thermal explosion furnace, closing a furnace door, and vacuumizing until the pressure in the furnace is lower than 10 Pa;
beginning to heat, and setting the heating speed to be 40K/min; heating to 1183K, then reducing the temperature to 1073K, preserving the heat for 10min, and simultaneously applying axial 30MPa pressure to the cylindrical pressed compact in the heat preservation process for 55 s; cooling the cylindrical ceramic-aluminum composite furnace which is densified by axial pressure to room temperature in vacuum after reaction;
(2) preparation of unrefined and strengthened aluminum alloy:
(2a) placing the pre-weighed aluminum alloy into a crucible, placing the crucible and the aluminum alloy into a crucible type resistance smelting furnace, and heating to 1023K; the aluminum alloy comprises the following components: Al-Si7-Mn0.65-Mg0.33。
(2b) After the alloy is completely melted, preserving heat for 30min, adding 0.05 wt.% of slag removing agent to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3) endogenous nano NbB2Strengthening treatment of the ceramic particles on the aluminum alloy:
(3a) after the weighed alloy is put into a crucible and is put into a furnace together with the crucible, the temperature is increased to 1123K;
(3b) after the alloy is completely melted, preserving heat for 30min, adding 0.05 wt.% of slag removing agent to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3c) will contain NbB2Adding ceramic particle reinforcer into the alloy liquid, NbB2The actual addition of ceramic particles was 0.3 wt.% (Nb/B mass ratio 4.30: 1; Nb/B molar ratio 1:2), and the mixed alloy liquid was subjected to ultrasonic treatment for 8 min;
(3d) casting the metal liquid after ultrasonic treatment into a metal mold, solidifying and cooling to obtain the nano NbB2Plate-like patterns of refined and strengthened aluminum alloy of ceramic particles.
Wherein, the metal mold in the step (3d) is made of the following materials: 45# steel, the size of the metal mold is as follows: 200mm by 150mm by 20 mm.
In-situ nano NbB2The ceramic particles can be used as an effective refining and strengthening agent of the aluminum alloy. FIG. 7 shows Al-Si7-Mn0.65-Mg0.33NbB in alloy2As-cast grain structure diagram with ceramic particles added in an amount of 0.3 wt.%. Compared with the aluminum alloy structure without the thinning treatment (as shown in figure 1), the aluminum alloy crystal grains added with the nano particles are thinned. FIG. 8 is an addition of 0.3 wt.% NbB2Al-Si of ceramic particles7-Mn0.65-Mg0.33Tensile stress strain curve of the alloy as cast. Addition of NbB2Yield strength sigma of as-cast aluminum alloy after nanoparticles0.2156.8MPa for (MPa), 225.8MPa for tensile strength UTS (MPa), strain at break εf(%) was 10.1%. Compared with the tensile property of the aluminum alloy without thinning and strengthening treatment (yield strength: 143.9MPa, tensile strength: 205.0MPa, breaking strain: 6.0 percent), NbB is added2The yield strength, tensile strength and breaking strain of the aluminum alloy of the nano particles are respectively improved by 9.0%, 10.2% and 68.3%, and the mechanical property is obviously improved, as shown in fig. 8 and table 1.
Example 4:
in-situ generated nano NbB in the embodiment2The method for grain refining and strengthening the aluminum alloy comprises the following steps:
(1) in-situ nano NbB2Particle refinement and preparation of a reinforcing agent:
(1a) b, ball milling activation pretreatment of boron powder: putting boron powder into a ball milling tank, and carrying out ball milling activation treatment on the boron powder for 1h at the speed of 300r/min by using a ball mill;
(1b) preparing powder used for a reaction pressed compact: weighing a certain amount of aluminum powder with the required granularity of 48 mu m, and carrying out ball milling treatment on the boron powder with the granularity of 1 mu m and the niobium powder with the granularity of 48 mu m for later use. The Al-Nb-B green compact is prepared by preparing 100g of mixed powder from aluminum powder, niobium powder and boron powder according to the following mixture ratio. Wherein the Al-Nb-B system reacts to generate nano NbB2Mass fraction of ceramic particles (Nb/B mass ratio 4.30: 1; Nb/B molar ratio 1:2) 30 wt.%: the aluminum powder, the niobium powder and the boron powder in the system respectively have the following weight: aluminum powder: 70 g; niobium powder: 24.33 g; boron powder: 5.67 g; preparing 100g of mixed powder;
(1c) ball-milling and mixing the powder used for the reaction pressed compact:
putting the prepared mixed powder with different components and zirconia grinding balls into a mixer, and filling ZrO with diameters of 5mm, 7mm, 11mm, 15mm, 20mm and 22mm into a tank 210 balls each of ZrO2The total ball mass is 800 g. Uniformly mixing for 25h at the speed of 40/min by using a mixer; wherein the mass ratio of the zirconia grinding ball to the mixed powder is 8: 1;
(1d) preparation of reaction green compacts:
taking out the powder of the ball-milling mixed material, wrapping the powder of the ball-milling mixed material with an aluminum foil, and performing cold pressing on the wrapped powder on a hydraulic press to obtain a phi 30 cylindrical pressed blank with the height of 35 mm; the density is 75%;
(1e) in-situ reaction of nanoparticles:
wrapping the phi 30 cylindrical pressed blank prepared in the step (2) by graphite paper, and putting the wrapped pressed blank into a graphite mold;
secondly, putting the graphite mould and the phi 30 cylindrical pressed blank into a vacuum thermal explosion furnace, closing a furnace door, and vacuumizing until the pressure in the furnace is lower than 10 Pa;
beginning to heat, and setting the heating speed to be 30K/min; heating to 1183K, then reducing the temperature to 1073K, preserving the heat for 10min, and simultaneously applying axial 25MPa pressure to the cylindrical pressed compact in the heat preservation process for 60 s; cooling the cylindrical ceramic-aluminum composite furnace which is densified by axial pressure to room temperature in vacuum after reaction;
(2) preparation of unrefined and strengthened aluminum alloy:
(2a) placing the pre-weighed aluminum alloy into a crucible, placing the crucible and the aluminum alloy into a crucible type resistance smelting furnace, and heating to 1023K; the aluminum alloy comprises the following components: Al-Si7-Mn0.65-Mg0.33；
(2b) After the alloy is completely melted, preserving heat for 30min, adding 0.05 wt.% of slag removing agent to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3) endogenous nano NbB2Strengthening treatment of the ceramic particles on the aluminum alloy:
(3a) after the weighed alloy is put into a crucible and is put into a furnace together with the crucible, the temperature is increased to 1123K;
(3b) after the alloy is completely melted, preserving heat for 30min, adding 0.05 wt.% of slag removing agent to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3c) will contain NbB2Adding ceramic particle reinforcer into the alloy liquid, NbB2The actual addition of ceramic particles was 0.3 wt.% (Nb/B mass ratio 4.30: 1; Nb/B molar ratio 1:2), and the mixed alloy liquid was subjected to ultrasonic treatment for 10 min;
(3d) casting the metal liquid after ultrasonic treatment into a metal mold, solidifying and cooling to obtain the nano NbB2Plate-like patterns of refined and strengthened aluminum alloy of ceramic particles.
Wherein, the metal mold in the step (3d) is made of the following materials: 45# steel, the size of the metal mold is as follows: 200mm by 150mm by 20 mm.
In-situ nano NbB2The ceramic particles can be used as an effective refining and strengthening agent of the aluminum alloy. FIG. 9 shows a structure in which Al-Si is present7-Mn0.65-Mg0.33NbB in alloy2As-cast grain structure diagram with ceramic particles added in an amount of 0.3 wt.%. Compared with the aluminum alloy structure without the thinning treatment (as shown in figure 1), the aluminum alloy crystal grains added with the nano particles are thinned. FIG. 10 is an addition of 0.3 wt.% NbB2Al-Si of ceramic particles7-Mn0.65-Mg0.33Tensile stress strain curve of the alloy as cast. Addition of NbB2Yield strength sigma of as-cast aluminum alloy after nanoparticles0.2(MPa) 152.4MPa, tensile strength UTS (MPa) 218.9MPa, strain at break εf(%) was 10.9%. Compared with the tensile property of the aluminum alloy without thinning and strengthening treatment (yield strength: 143.9MPa, tensile strength: 205.0MPa, breaking strain: 6.0 percent), NbB is added2The yield strength, tensile strength and breaking strain of the aluminum alloy of the nano particles are respectively improved by 6.0%, 6.3% and 81.7%, and the mechanical property is obviously improved, as shown in figure 10 and table 1.
Example 5:
in-situ generated nano NbB in the embodiment2The method for grain refining and strengthening the aluminum alloy comprises the following steps:
(1) in-situ nano NbB2Particle refinement and preparation of a reinforcing agent:
(1a) b, ball milling activation pretreatment of boron powder: putting boron powder into a ball milling tank, and carrying out ball milling activation treatment on the boron powder for 1h at the speed of 300r/min by using a ball mill;
(1b) preparing powder used for a reaction pressed compact: weighing a certain amount of aluminum powder with the required granularity of 25 mu m, and carrying out ball milling treatment on the boron powder with the granularity of 1 mu m and the niobium powder with the granularity of 48 mu m for later use. The Al-Nb-B green compact is prepared by preparing 100g of mixed powder from aluminum powder, niobium powder and boron powder according to the following mixture ratio. Wherein the Al-Nb-B system reacts to generate nano NbB2Mass fraction of ceramic particles (Nb/B mass ratio 4.30: 1; Nb/B molar ratio 1:2) 40 wt.%: the aluminum powder, the niobium powder and the boron powder in the system respectively have the following weight: aluminum powder: 60 g; niobium powder: 32.45 g; boron powder: 7.55 g; preparing 100g of mixed powder;
(1c) ball-milling and mixing the powder used for the reaction pressed compact: putting the prepared mixed powder with different components and zirconia grinding balls into a mixer, and filling ZrO with diameters of 5mm, 7mm, 11mm, 15mm, 20mm and 22mm into a tank 210 balls each of ZrO2The total ball mass is 800 g. Uniformly mixing for 20 hours at the speed of 45/min by using a mixer; wherein the mass ratio of the zirconia grinding ball to the mixed powder is 8: 1;
(1d) preparation of reaction green compacts: taking out the powder of the ball-milling mixed material, wrapping the powder of the ball-milling mixed material with an aluminum foil, and performing cold pressing on the wrapped powder on a hydraulic press to obtain a phi 30 cylindrical pressed blank with the height of 45 mm; the density is 65%;
(1e) in-situ reaction of nanoparticles:
wrapping the phi 30 cylindrical pressed blank prepared in the step (2) by graphite paper, and putting the wrapped pressed blank into a graphite mold;
secondly, putting the graphite mould and the phi 30 cylindrical pressed blank into a vacuum thermal explosion furnace, closing a furnace door, and vacuumizing until the pressure in the furnace is lower than 10 Pa;
beginning to heat, and setting the heating speed to be 40K/min; heating to 1183K, then reducing the temperature to 1073K, preserving the heat for 10min, and simultaneously applying axial 35MPa pressure to the cylindrical pressed compact in the heat preservation process for 48 s; cooling the cylindrical ceramic-aluminum composite furnace which is densified by axial pressure to room temperature in vacuum after reaction;
(2) preparation of unrefined and strengthened aluminum alloy:
(2a) placing the pre-weighed aluminum alloy into a crucible, placing the crucible and the aluminum alloy into a crucible type resistance smelting furnace, and heating to 1023K; the aluminum alloy comprises the following components: Al-Si10-Cu-Mg0.39；
(2b) After the alloy is completely melted, preserving heat for 30min, adding 0.10 wt.% slag remover to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3) endogenous nano NbB2Strengthening treatment of the ceramic particles on the aluminum alloy:
(3a) after the weighed alloy is put into a crucible and is put into a furnace together with the crucible, the temperature is increased to 1123K;
(3b) after the alloy is completely melted, preserving heat for 30min, adding 0.10 wt.% slag remover to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3c) will contain NbB2Adding ceramic particle reinforcer into the alloy liquid, NbB2The actual addition of ceramic particles was 0.3 wt.% (Nb/B mass ratio 4.30: 1; Nb/B molar ratio 1:2), and the mixed alloy liquid was subjected to ultrasonic treatment for 10 min;
(3d) casting the metal liquid after ultrasonic treatment into a metal mold, solidifying and cooling to obtain the nano NbB2Plate-like patterns of refined and strengthened aluminum alloy of ceramic particles.
Wherein, the metal mold in the step (3d) is made of the following materials: 45# steel, the size of the metal mold is as follows: 200mm by 150mm by 20 mm.
In-situ nano NbB2The ceramic particles can be used as an effective refining and strengthening agent of the aluminum alloy. FIG. 11 shows a structure in which Al-Si is present10-Cu-Mg0.39NbB in alloy2As-cast grain structure diagram with ceramic particles added in an amount of 0.3 wt.%. Compared with the aluminum alloy structure without the thinning treatment (as shown in figure 2), the aluminum alloy crystal grains added with the nano particles are thinned. FIG. 12 is an addition of 0.3 wt.% NbB2Al-Si of ceramic particles10-Cu-Mg0.39As-cast tensile curve of the alloy. Addition of NbB2Yield strength sigma of as-cast aluminum alloy after nanoparticles0.2141.8MPa for (MPa), 279.6MPa for UTS (MPa) for tensile strength and ε for breaking strainf(%) was 14.3%. Compared with the tensile property of the aluminum alloy without thinning and strengthening treatment (yield strength: 141.8MPa, tensile strength: 249.7MPa and breaking strain: 11.7 percent), NbB is added2After the nanoparticles are formed, the tensile strength and the breaking strain of the alloy are respectively improved by 12.0% and 22% compared with those of the untreated alloy, and the mechanical property is improved, as shown in fig. 12 and table 1.
The structure and properties of the aluminum alloys were measured for the materials of the above examples, and the following data were obtained: table 1 shows the different aluminum alloy substrates, different nanometer NbBs in examples 1-52The addition amount of ceramic particles and the tensile property value of the alloy under different preparation process parameters.
TABLE 1
Sample (I) σ0.2(MPa) UTS(MPa) εf(％)
Al-7Si-0.65Mn-0.33Mg 143.9 205.0 6.0
Al-10Si-1Cu-0.39Mg 141.8 249.7 11.7
Examples 1 163.2 238.0 8.8
EXAMPLES example 2 168.7 255.2 8.6
EXAMPLE 3 156.8 225.8 10.1
EXAMPLE 4 152.4 218.9 10.9
EXAMPLE 5 141.8 279.6 14.3
The microstructure and the mechanical property of the material are obviously optimized: under the conditions of optimal refinement and strengthening (NbB in Al-7Si-0.65Mn-0.33Mg alloy)2The addition amount of the ceramic particles is 0.1 wt.%, and Nb/B is 1:2), the crystal grains of the aluminum alloy are obviously refined, and the yield strength, the tensile strength and the breaking strain of the alloy in an as-cast state are respectively 168.7MPa, 255.2MPa and 8.6 percent. The yield strength, the tensile strength and the breaking strain of the aluminum alloy without thinning and strengthening treatment in an as-cast state are 143.9MPa and 205.0 respectivelyMPa, 6.0 percent. By adding NbB2After the aluminum alloy is refined and strengthened by the nano particles, the yield strength, the tensile strength and the fracture strain of the alloy are respectively improved by 17.2 percent, 24.5 percent and 43.3 percent compared with the untreated alloy, and the mechanical property is obviously improved.
While the foregoing is directed to the preferred embodiment of the present invention, it will be understood by those skilled in the art that various changes and modifications may be made without departing from the spirit and scope of the invention.

Claims (2)

1. In-situ generated nano NbB2The method for grain refining and strengthening the aluminum alloy is characterized by comprising the following steps: the method comprises the following steps:
(1) in-situ nano NbB2Particle refinement and preparation of a reinforcing agent:
(1a) b, ball milling activation pretreatment of boron powder: putting boron powder into a ball milling tank, and carrying out ball milling activation treatment on the boron powder for 1-3 h at the speed of 200-300 r/min by using a ball mill;
(1b) preparing powder used for a reaction pressed compact: weighing aluminum powder with the required particle size of 13-48 mu m, and performing ball milling treatment on boron powder with the particle size of 0.5-1 mu m, niobium powder with the particle size of 48 mu m and copper powder with the particle size of 45 mu m for later use; the Al-Nb-B-Cu green compact is prepared by preparing 100g of mixed powder from aluminum powder, niobium powder, boron powder and copper powder according to the following mixture ratio:
firstly, reacting in Al-Nb-B system to generate nano NbB2The mass fraction of ceramic particles was 10 wt.%; the aluminum powder, the niobium powder, the boron powder and the copper powder in the system respectively have the following weight: aluminum powder: 90 g; niobium powder: 8.11 g; boron powder: 1.89 g; copper powder: 0 g; preparing 100g of mixed powder; wherein, the nanometer NbB2The Nb/B mass ratio in the ceramic particles is 4.30: 1;
② the nano NbB is generated by the reaction in the Al-Nb-B system2Mass fraction of ceramic particles 20 wt.%; the aluminum powder, the niobium powder, the boron powder and the copper powder in the system respectively have the following weight: aluminum powder: 80 g; niobium powder: 16.22 g; boron powder: 3.78 g; copper powder: 0 g; preparing 100g of mixed powder; wherein, the nanometer NbB2The Nb/B mass ratio in the ceramic particles is 4.30: 1;
③ reaction in Al-Nb-B system to generate nanometer NbB2Mass fraction of ceramic particles 30 wt.%; the aluminum powder, the niobium powder, the boron powder and the copper powder in the system respectively have the following weight: aluminum powder: 70 g; niobium powder: 24.33 g; boron powder: 5.67 g; copper powder: 0 g; preparing 100g of mixed powder; wherein, the nanometer NbB2The Nb/B mass ratio in the ceramic particles is 4.30: 1;
reacting in Al-Nb-B system to generate nano NbB2Mass fraction of ceramic particles 40 wt.%; the aluminum powder, the niobium powder, the boron powder and the copper powder in the system respectively have the following weight: aluminum powder: 60 g; niobium powder: 32.45 g; boron powder: 7.55 g; copper powder: 0 g; preparing 100g of mixed powder; wherein, the nanometer NbB2The Nb/B mass ratio in the ceramic particles is 4.30: 1;
reacting in Al-Nb-B-Cu system to generate NbB2The mass fraction of the ceramic particles was 30 wt.%, wherein the content of Cu element was 5 wt.%; the aluminum powder, the niobium powder, the boron powder and the copper powder in the system respectively have the following weight: aluminum powder: 65 g; niobium powder: 24.33 g; boron powder: 5.67 g; copper powder: 5 g; preparing 100g of mixed powder;
(1c) ball-milling and mixing the powder used for the reaction pressed compact: putting the prepared mixed powder with different components and zirconia grinding balls into a mixer, and filling ZrO with diameters of 5mm, 7mm, 11mm, 15mm, 20mm and 22mm into a tank210 balls each of ZrO2The ball mass is 800 g; uniformly mixing for 8-32 h at the speed of 30-60 r/min by using a mixer; wherein the mass ratio of the zirconia grinding ball to the mixed powder is 8: 1;
(1d) preparation of reaction green compacts: taking out the powder of the ball-milling mixed material, wrapping the powder of the ball-milling mixed material with an aluminum foil, and performing cold pressing on the wrapped powder on a hydraulic press to obtain a phi 30 cylindrical pressed blank with the height of 35-45 mm; the density is 60-75%;
(1e) in-situ reaction of nanoparticles:
wrapping the prepared phi 30 cylindrical pressed blank by graphite paper and putting the wrapped pressed blank into a graphite mold;
secondly, putting the graphite mould and the phi 30 cylindrical pressed blank into a vacuum thermal explosion furnace, closing a furnace door, and vacuumizing until the pressure in the furnace is lower than 10 Pa;
beginning to heat, and setting the heating speed to be 25-40K/min; heating to 1183K, then reducing the temperature to 1073K, preserving the heat for 10min, and applying axial pressure of 25-55 MPa to the cylindrical pressed compact in the heat preservation process for 20-60 s; cooling the cylindrical ceramic-aluminum compound which is densified by axial pressure to room temperature along with the furnace in vacuum after reaction;
(2) preparation of unrefined and strengthened aluminum alloy:
(2a) placing the pre-weighed aluminum alloy into a crucible, placing the crucible and the aluminum alloy into a crucible type resistance smelting furnace, and heating to 1023K; the aluminum alloy comprises the following components: Al-Si7-Mn0.65-Mg0.33、Al-Si10-Cu-Mg0.39；
(2b) After the alloy is completely melted, preserving heat for 30min, adding 0.05-0.10 wt.% of slag removing agent to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3) in-situ nano NbB2Strengthening treatment of the ceramic particles on the aluminum alloy:
(3a) after the weighed alloy is put into a crucible and is put into a furnace together with the crucible, the temperature is increased to 1123K;
(3b) after the alloy is completely melted, preserving heat for 30min, adding 0.05-0.10 wt.% of slag removing agent to refine and remove slag from the alloy liquid, and preserving heat for 10min after slag removal treatment;
(3c) will contain NbB2Adding ceramic particle reinforcer into the alloy liquid, NbB2The actual adding amount of the ceramic particles is 0.1-0.3 wt%, and the mixed alloy liquid is subjected to ultrasonic treatment for 3-10 min;
(3d) casting the metal liquid after ultrasonic treatment into a metal mold, solidifying and cooling to obtain the nano NbB2Plate-like patterns of refined and strengthened aluminum alloy of ceramic particles.
2. The in-situ nano NbB as claimed in claim 12The method for grain refining and strengthening the aluminum alloy is characterized by comprising the following steps: the metal mold in the step (3d) is made of the following materials: 45# SteelThe size of the metal mold is as follows: 200mm by 150mm by 20 mm.
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Publication number Priority date Publication date Assignee Title
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US20210046553A1 (en) * 2019-04-19 2021-02-18 Sumitomo Electric Hardmetal Corp. Cutting tool
WO2020213264A1 (en) * 2019-04-19 2020-10-22 住友電工ハードメタル株式会社 Cutting tool
CN110181193B (en) * 2019-05-17 2021-01-08 江西理工大学 Novel Al-Mg-Ti alloy welding wire and preparation method thereof
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CN110512125B (en) * 2019-08-30 2020-09-22 中国航发北京航空材料研究院 Preparation method of diameter aluminum-lithium alloy wire for additive manufacturing
CN110560957B (en) * 2019-09-03 2021-07-30 北京工业大学 Micro-nano particle reinforced aluminum alloy flux-cored filling wire for welding 7075 aluminum alloy
CN110625297B (en) * 2019-09-19 2021-02-12 北京科技大学 Preparation method of high-strength and high-toughness steel welding wire containing nano particles
CN110656264A (en) * 2019-11-05 2020-01-07 东北轻合金有限责任公司 Manufacturing method of aluminum alloy wire for protective fence
CN110747361A (en) * 2019-11-20 2020-02-04 中南大学 Preparation method of titanium boride reinforced aluminum-based composite material based on ultrasonic and mechanical stirring
CN111101026A (en) * 2019-12-06 2020-05-05 江苏理工学院 Preparation method of high-strength high-toughness aluminum-based composite material
CN111097911B (en) * 2019-12-12 2022-04-26 南方科技大学 Ceramic-metal composite foam material and preparation method thereof
CN111304562A (en) * 2019-12-14 2020-06-19 江苏时代华宜电子科技有限公司 High-modulus cast ceramic-aluminum high-purity material and preparation method thereof
CN111057906A (en) * 2019-12-30 2020-04-24 苏州再超冶金制品有限公司 Nano ceramic powder reinforced alloy composite material and preparation method thereof
CN111139385B (en) * 2019-12-31 2021-06-15 上海交通大学 Aluminum alloy welding wire containing ceramic particles and preparation method and application thereof
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CN111690857A (en) * 2020-05-13 2020-09-22 宁波华源精特金属制品有限公司 Engine connecting rod
CN111411270B (en) * 2020-05-21 2021-03-19 滨州渤海活塞有限公司 Method for changing morphology of ferrosilicon phase in aluminum alloy
CN111850351A (en) * 2020-07-01 2020-10-30 吉林大学 Method for preparing high-elongation cast-rolling Al-Mn series aluminum alloy plate blank
CN111809075B (en) * 2020-07-03 2021-07-06 西安石油大学 Ti coating Ti3AlC2Particle reinforced Al-based internal combustion engine piston connecting rod and manufacturing method thereof
CN112264732B (en) * 2020-10-16 2023-11-14 大连理工大学 Welding wire for copper/steel dissimilar welding, preparation method of welding wire and copper/steel dissimilar welding method
CN112251646A (en) * 2020-10-21 2021-01-22 吉林大学 Titanium alloy powder of endogenous nano composite ceramic particles and preparation method and application thereof
CN112210694B (en) * 2020-10-21 2022-04-19 吉林大学 Nanoparticle toughened ZTC4 titanium alloy and preparation method thereof
CN112593110B (en) * 2020-12-11 2021-09-10 迈特李新材料(深圳)有限公司 Preparation method of nano-carbide reinforced aluminum matrix composite welding wire
CN112746195B (en) * 2020-12-30 2022-02-01 吉林大学 Recession-resistant refiner, preparation method and application thereof, aluminum alloy and refining method thereof
CN113042748B (en) * 2021-03-09 2022-10-11 中北大学 Method for preparing high-strength high-elongation Al-Cu-Mg alloy by SLM
CN113084395B (en) * 2021-03-25 2022-09-13 山东滨州华创金属有限公司 Aluminum alloy welding wire preparation method and aluminum alloy welding wire prepared by same
CN113106276B (en) * 2021-04-10 2022-03-01 中北大学 Preparation method of multi-component cooperative strengthening aluminum matrix composite
CN113210573B (en) * 2021-04-20 2024-04-05 扬州戴卡轮毂制造有限公司 Aluminum alloy hub and multi-field coupling casting forming and grain refinement method thereof
CN113414365A (en) * 2021-05-14 2021-09-21 江苏大学 Aluminum alloy hub blank manufacturing equipment and working method thereof
CN113416861A (en) * 2021-05-17 2021-09-21 江苏大学 Preparation method of micro-nano dual-scale TiC particle reinforced aluminum matrix composite material
CN113373367A (en) * 2021-06-04 2021-09-10 江西理工大学 Aluminum intermediate alloy containing multi-scale mixed particles and preparation method thereof
CN113373355A (en) * 2021-06-09 2021-09-10 江西理工大学 Multi-scale particle modified 7000 series alloy wire and preparation method thereof
CN113385855A (en) * 2021-06-09 2021-09-14 江西理工大学 Multi-scale particle modified Al-Mg alloy welding wire and preparation method thereof
CN113737037A (en) * 2021-09-17 2021-12-03 苏州明志科技股份有限公司 Method for refining aluminum alloy grains
CN113909454A (en) * 2021-10-09 2022-01-11 大冶市东晟机械制造有限公司 Low-pressure casting process for rear hub of alloy automobile
CN113909733B (en) * 2021-10-11 2023-06-09 河北科技大学 Aluminum magnesium alloy welding wire for arc fuse additive manufacturing and preparation method thereof
CN114350993B (en) * 2021-12-30 2023-04-07 安徽科蓝特铝业有限公司 Production process of high-strength aluminum alloy applied to bicycle frame
CN114790522A (en) * 2022-04-29 2022-07-26 山东裕航特种合金装备有限公司 Preparation method of electronic material containing nano ceramic aluminum alloy material
CN114908266B (en) * 2022-05-12 2023-09-22 昆明理工大学 Preparation method of aluminum-based composite material wire rod for 3D printing
CN114703390B (en) * 2022-06-06 2022-09-09 中国航发北京航空材料研究院 Refining agent and refining and purifying method of aluminum alloy cast on line by combining refining agent with argon
CN115159450B (en) * 2022-07-03 2024-02-23 复旦大学 NbB-based 2 Catalytic lifting of MgH 2 Method for hydrogen storage performance
CN115070038B (en) * 2022-07-21 2022-11-04 西安稀有金属材料研究院有限公司 In-situ mixed dual-phase ceramic reinforced iron-based composite material and preparation method thereof
CN115430843A (en) * 2022-08-16 2022-12-06 上海交通大学 Double-phase particle reinforced additive aluminum alloy and preparation method thereof
CN115740832B (en) * 2022-10-18 2023-11-07 江苏鑫华能环保工程股份有限公司 Carbon fiber reinforced magnesium alloy welding material and preparation method thereof
CN115896524B (en) * 2022-11-19 2024-03-08 吉林大学 Method for improving segregation and strength of cast superalloy through micro-nano particles
CN116179884B (en) * 2022-12-28 2024-06-25 吉林大学 Vacuum induction smelting method for preparing titanium-coated NbB2Method for reinforcing TiAl alloy by nano particles
CN116240443B (en) * 2022-12-28 2024-06-25 吉林大学 Nano ceramic particle reinforced stainless steel and preparation method thereof
CN116200625B (en) * 2022-12-28 2024-06-25 吉林大学 Nanoparticle modified aluminum alloy and preparation method thereof
CN116179883B (en) * 2022-12-28 2024-06-25 吉林大学 Nanometer NbB2Preparation method of particle reinforced NiAl alloy
CN116159995B (en) * 2023-03-02 2023-11-17 阳江普利餐厨用品有限公司 Powder material for metal additive and application thereof in production of cladding coating
CN116716508A (en) * 2023-06-12 2023-09-08 昆明理工大学 TiB (titanium-boron) 2 TiC ceramic reinforced aluminum alloy matrix composite piston and preparation method thereof

Family Cites Families (76)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
NO163966C (en) * 1983-11-29 1990-08-15 Moltech Invent Sa ALUMINUM REDUCTION CELL.
US4690796A (en) * 1986-03-13 1987-09-01 Gte Products Corporation Process for producing aluminum-titanium diboride composites
JPS63312923A (en) * 1987-06-17 1988-12-21 Agency Of Ind Science & Technol Wire preform material for carbon fiber reinforced aluminum composite material
US4909842A (en) * 1988-10-21 1990-03-20 The United States Of America As Represented By The United States Department Of Energy Grained composite materials prepared by combustion synthesis under mechanical pressure
US5104456A (en) * 1990-02-15 1992-04-14 Colorado School Of Mines Process for optimizing titanium and zirconium additions to aluminum welding consumables
US5256368A (en) * 1992-07-31 1993-10-26 The United States Of America As Represented By The Secretary Of The Interior Pressure-reaction synthesis of titanium composite materials
JP3417217B2 (en) * 1996-06-07 2003-06-16 トヨタ自動車株式会社 Method for producing titanium carbide particle-dispersed metal matrix composite material
JPH10219312A (en) * 1997-02-10 1998-08-18 Toyota Motor Corp Titanium carbide dispersion-strengthened aluminum-base powder, its production and titanium carbide dispersion-strengthened aluminum-base composite material
NO990813L (en) * 1999-02-19 2000-08-21 Hydelko Ks Alloy for grain refinement of aluminum alloys
CN1079443C (en) * 1999-06-24 2002-02-20 东南大学 Titanium carbide reinforced antiwear aluminium alloy and its preparing process
CN1161483C (en) * 2001-03-23 2004-08-11 中国科学院金属研究所 High-strength in-situ Al-base composition
US6899844B2 (en) * 2001-04-25 2005-05-31 Taiho Kogyo Co., Ltd. Production method of aluminum alloy for sliding bearing
CN1555423A (en) * 2001-07-25 2004-12-15 �Ѻ͵繤��ʽ���� Aluminum alloy excellent in machinability, and aluminum alloy material and method for production thereof
CN1228464C (en) * 2003-06-20 2005-11-23 吉林大学 Method for preparing two-phase granular mixed reinforced magnesium alloy based composite material
CN1250760C (en) * 2003-10-30 2006-04-12 上海交通大学 Method for preparing aluminium based composite material intensified by interlarding in situ
CN1298877C (en) * 2004-03-11 2007-02-07 山东理工大学 Method for manufacturing ceramic particle reinforced aluminium-based nano composite material
CN100422368C (en) * 2004-07-05 2008-10-01 北京有色金属研究总院 In situ formed TiC reinforced Al-Fe-V-Si series heat resistant aluminium alloy material and its preparation method
FR2875153B1 (en) * 2004-09-10 2008-02-01 Pechiney Aluminium SUPPORT WIRE FOR WELDING ALUMINUM ALLOYS
CN100396650C (en) * 2006-10-30 2008-06-25 陕西科技大学 Method for preparing Ti2AlC ceramic material
CN100443605C (en) * 2006-12-28 2008-12-17 上海交通大学 Preparation method of granule-mixed reinforced aluminium-based composite material
CN100460136C (en) * 2007-01-30 2009-02-11 山东大学 Filling metal particle for welding and manufacturing method therefor
CN101214540A (en) * 2008-01-07 2008-07-09 吉林大学 Method for preparing TiC/TiB2 biphase ceramic granule partial reinforced manganese steel composite material
CN101758203B (en) * 2008-11-12 2013-04-03 郑东海 Process for smelting and lower-pressure casting of aluminum alloy wheel hub
CN101775513B (en) * 2009-11-11 2012-05-30 昆明理工大学 Method for preparing (TiB2+TiC) dispersion-strengthened copper-based composite material by mechanical alloying
CN101775514A (en) * 2009-11-11 2010-07-14 昆明理工大学 Method for preparing (TiB2+TiC) dispersion-strengthening copper-based composites by adopting self-propagating high-temperature synthesis
CN101876017B (en) * 2009-12-15 2012-02-29 哈尔滨工业大学 Preparation method of nano-ceramic particle reinforced aluminum foam matrix composite material
CN101760674B (en) * 2010-02-05 2012-11-07 哈尔滨工业大学 Roll forming technique of board made of NiAl-based composite material
CN102260814B (en) * 2011-07-26 2013-01-09 吉林大学 In situ nano TiC ceramic particle reinforced aluminum based composite material and preparation method thereof
CN103842534A (en) * 2011-09-19 2014-06-04 美铝有限责任公司 Improved aluminum casting alloys containing vanadium
CN102366828B (en) * 2011-10-10 2016-12-21 陈丹红 A kind of low-pressure casting method of aluminium alloy automobile hub
CN102430757A (en) * 2011-11-25 2012-05-02 天津大学 Method for preparing TiB2/TiC (titanium diboride/titanium carbide) ultrafine powder for surface spraying of engine piston ring by means of high energy ball milling
CN102584242B (en) * 2012-02-28 2013-08-14 吉林大学 High-temperature high-pressure preparation method for titanium diboride
CN102644010B (en) * 2012-04-11 2014-06-18 北京工业大学 Al-Ti-B-Er refiner and preparation method thereof
CN102747254B (en) * 2012-07-27 2013-10-16 哈尔滨工业大学 Preparation process of reinforced intragranular aluminum matrix composites with nano ceramic particles added externally
CN102787252B (en) * 2012-08-14 2014-05-21 大连理工大学 Method for preparing TiB2 reinforced aluminium matrix composite in situ
CN102839306B (en) * 2012-09-17 2014-05-07 东北轻合金有限责任公司 Manufacturing method of aluminum alloy welding wire for aerospace
CN102876919B (en) * 2012-09-27 2014-05-21 南京航空航天大学 In-situ synthesized TiC particle-reinforced titanium aluminium alloy material and preparation method thereof
KR20140063024A (en) * 2012-11-16 2014-05-27 현대자동차주식회사 Aluminum wheel and method for producing the same
CN103192064A (en) * 2013-04-25 2013-07-10 丹阳百斯特新型合金科技有限公司 Al-Ti-B-C refiner and preparation method
CN103266243A (en) * 2013-06-06 2013-08-28 中南林业科技大学 High performance aluminum alloy for low pressure casting of minicar structural member and preparation method of high performance aluminum alloy
CN104372207B (en) * 2013-08-12 2016-06-22 大力神铝业股份有限公司 A kind of soldering 4004 aluminium alloys
CN103572111A (en) * 2013-11-20 2014-02-12 江苏江旭铸造集团有限公司 High-strength and toughness cast aluminum alloy
CN103817495B (en) * 2014-03-05 2016-06-08 浙江巨科实业股份有限公司 Manufacturing method of aluminum alloy hub
CN104263988B (en) * 2014-05-04 2016-08-24 昆明理工大学 A kind of TiB2the preparation method of particle reinforced aluminum foam/aluminium alloy
CN104120291B (en) * 2014-07-22 2017-06-13 上海交通大学 A kind of TiC, TiB2The preparation method of particle enhanced nickel base composite material
CN104209498B (en) * 2014-07-24 2017-02-15 昆明理工大学 Preparing method of interface modification layer of ceramic particle enhanced metal base composite material
CN104264001B (en) * 2014-09-16 2016-08-17 广东新劲刚新材料科技股份有限公司 In-situ synthesized particle reinforced aluminum matrix composite material and preparation method thereof
CN104372208B (en) * 2014-10-28 2019-03-29 赵遵成 A kind of endogenetic particle hybrid reinforced aluminum-matrix composite material and preparation method thereof
CN104532068B (en) * 2014-12-15 2016-08-17 河海大学 Nano TiC ceramic particle reinforced aluminium base composite material and preparation method thereof
CN104532044B (en) * 2014-12-18 2017-01-25 兰州理工大学 Low-cost and high-efficiency Al-Ti-C-Ce refining agent and preparation method thereof
CN105671350A (en) * 2015-03-19 2016-06-15 中信戴卡股份有限公司 Aluminum alloy refiner, preparation method therefor and use thereof
CN104789811B (en) * 2015-04-03 2016-09-28 昆明冶金研究院 A kind of preparation method of Al-Ti-B intermediate alloy
CN104946920B (en) * 2015-06-17 2017-01-11 广东省材料与加工研究所 Preparation method of grain refiner
CN105002407A (en) * 2015-08-13 2015-10-28 枞阳县金源汽车零部件有限公司 Aluminum profile for automobile wheels and preparation method of aluminum profile
CN105149590A (en) * 2015-08-28 2015-12-16 苏州莱特复合材料有限公司 Powder metallurgy gear and manufacturing method thereof
CN105132733B (en) * 2015-09-29 2017-10-13 华中科技大学 A kind of method for preparing nanoparticle reinforced aluminum-based composite
CN105525157A (en) * 2016-02-17 2016-04-27 苏州华冲精密机械有限公司 Aluminum alloy automobile hub casting process
CN105689687A (en) * 2016-03-01 2016-06-22 刘加兴 High-pressure and low-pressure casting process and equipment for aluminum alloy casting products
CN105734387B (en) * 2016-03-17 2018-02-23 中南大学 A kind of TiB2Based ceramic metal and preparation method thereof
CN105728734B (en) * 2016-03-24 2017-10-20 西安工业大学 High-strength superfine ultra-fine（TixBy‑TiC）/ 7075Al composites and preparation method thereof
CN105779831B (en) * 2016-05-25 2017-08-29 桂林航天工业学院 Aero-Space aluminium alloy welding wire and preparation method thereof
CN105886853A (en) * 2016-06-01 2016-08-24 上海交通大学 Nano ceramic particle reinforced aluminum silicon alloy, preparation method and application thereof
CN105886847A (en) * 2016-06-01 2016-08-24 上海交通大学 High-temperature-resistant ceramic nanoparticle reinforced aluminum alloy and preparation method and application thereof
CN105908024A (en) * 2016-06-21 2016-08-31 上海交通大学 High-temperature-resistant nano ceramic particle reinforced cocrystallized Al-Si alloy and casting method thereof
CN106086538A (en) * 2016-06-21 2016-11-09 上海交通大学 High-temperature resistant nano ceramic particle strengthens hypoeutectic al-si alloy and casting method thereof
CN105970037B (en) * 2016-07-15 2017-09-22 南南铝业股份有限公司 Overpass aluminium alloy and preparation method thereof
CN106086488B (en) * 2016-07-15 2017-09-22 南南铝业股份有限公司 Subway station furred ceiling aluminium alloy and preparation method thereof
CN106271189B (en) * 2016-08-24 2018-09-14 上海交通大学 A kind of preparation method of welding wire or welding rod with small grains tissue
CN106086546B (en) * 2016-08-26 2017-08-25 山东金马汽车装备科技有限公司 The low-pressure casting process of aluminium alloy wheel hub
CN106756352B (en) * 2016-11-22 2018-04-06 昆明理工大学 Raw Cr in one kind2B and MgO diphase particles strengthen the preparation method of magnesium-based composite material
CN106756264B (en) * 2016-11-24 2019-06-21 湖南江滨机器（集团）有限责任公司 A kind of aluminum matrix composite, preparation method and its application
CN106591618A (en) * 2016-12-06 2017-04-26 昆明理工大学 Preparation method of endogenous double-phase particle enhanced aluminum-based composite material
CN106756319A (en) * 2016-12-13 2017-05-31 中国科学院金属研究所 A kind of aluminium alloy and aluminum matrix composite for preparing high-strength high-plastic aluminum matrix composite
CN107043901B (en) * 2017-02-23 2019-01-08 吉林大学 Basalt fibre and ceramic particle mix aluminium drill pipe material and preparation method thereof
CN107254610A (en) * 2017-06-12 2017-10-17 吉林大学 Raw nano-sized particles reinforced aluminium alloy material preparation method in a kind of
CN107419126B (en) * 2017-07-04 2019-04-02 北京理工大学 A kind of TiB-TiB2The fast preparation method of-Al composite ceramics

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