CN114959330A - Light metal composite material with high strength and toughness and low thermal expansion coefficient and preparation method thereof - Google Patents
Light metal composite material with high strength and toughness and low thermal expansion coefficient and preparation method thereof Download PDFInfo
- Publication number
- CN114959330A CN114959330A CN202210049620.9A CN202210049620A CN114959330A CN 114959330 A CN114959330 A CN 114959330A CN 202210049620 A CN202210049620 A CN 202210049620A CN 114959330 A CN114959330 A CN 114959330A
- Authority
- CN
- China
- Prior art keywords
- coge
- thermal expansion
- powder
- az91d
- negative thermal
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0408—Light metal alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
- B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention discloses a preparation method of a light metal composite material with high strength and toughness and low thermal expansion coefficient, which comprises the following steps: firstly, preparing a negative thermal expansion material Mn x CoGe, wherein x is more than or equal to 0.9 and less than or equal to 1; secondly, obtaining Mn by sintering x CoGe/AZ91D composite: 1) adding Mn as negative thermal expansion material x Mixing CoGe and metal matrix powder in proportion, and fully grinding to obtain Mn x CoGe/AZ91D mixed powder, negative thermal expansion material Mn x The mass ratio of the CoGe to the metal matrix powder is 3-7: 93-97; the metal matrix is pure magnesium or magnesium alloy, or pure aluminum and alloy thereof; 2) adding Mn x CoGe/AZ91D was placed in a mold, and vacuum was applied to 1 in a hot pressing sintering furnaceAnd (3) increasing the temperature from room temperature to 500-600 ℃ at the temperature increase rate of 5-25 ℃/min, simultaneously pressurizing to 23-27 MPa, keeping the temperature and the pressure for 50-70 minutes, and cooling to obtain the product.
Description
Technical Field
The invention relates to the technical field of metal composite materials, in particular to a light metal composite material with high strength and toughness and a low thermal expansion coefficient and a preparation method thereof.
Background
In general, most objects exhibit "positive thermal expansion" characteristics, i.e., the volume of the object increases with increasing temperature, while maintaining a constant pressure. The characteristic of the material causes thermal stress generated in the process of expansion with heat and contraction with cold of some parts which are in service at higher temperature, when the stress is accumulated to a certain degree, the aging of the parts is accelerated, the service performance is reduced, and even the parts are directly caused to generate destructive cracks to fail. For example, metal structures and parts applied in the aerospace field and the space environment generally undergo drastic changes of environmental temperature, and the difference of Coefficients of Thermal Expansion (CTE) between different materials not only causes great internal stress in the structures and the parts, but also causes changes of surface contact state and tribological design (such as changes of original matching of structures such as holes, pins, keys and the like), thereby causing functional failure, and in severe cases, causing microcracks and structural damage to the parts; in the aspect of information storage and transmission, the microstructure and shape change of materials and devices caused by thermal expansion and cold contraction can cause information distortion and transmission failure; in addition, the precision of the appearance and the slight change of the size of components in precision systems such as a micro electro mechanical system are both important to the functions of the components, but the service environment of the components is always subjected to larger temperature change, so the thermal expansion or shrinkage of the materials has obvious influence on the performance stability of the components, the service life of the system and the application range. Especially in precision instruments such as aerospace, the change in volume of parts caused by thermal expansion will cause the device to lose function.
Negative thermal expansion is the phenomenon whereby a material shrinks rather than expands when heated. Although negative thermal expansion at low temperatures has been observed previously in some simple materials, it was not discovered until 1996 that some materials had negative thermal expansion over a very wide temperature range, which led to concern about the phenomenon of negative thermal expansion. For a long time, exploring and preparing new compound materials with low expansion coefficient, near zero and even negative expansion coefficient are always valued by research teams at home and abroad. The material with negative thermal expansion characteristic and the material with positive thermal expansion behavior are compounded to realize the regulation and control of the whole CTE of the material, and the composite material with ultralow thermal expansion or near-zero expansion is developed to improve the thermal shock resistance of the material and solve the problems of fatigue fracture, microcrack, thermal stress and the like caused by the CTE mismatching of the material, thereby reducing the production cost and improving the social benefit and the economic benefit.
Metals have excellent mechanical properties, high melting point and high ductility, and are often used as various structural members. The magnesium alloy is one of the lightest alloy materials, has high specific strength and specific stiffness, excellent anti-electromagnetic interference capability and good machinability due to low density, belongs to an environment-friendly material, is known as a green material with the most development prospect in the twenty-first century, and is widely applied to the preparation of precision parts in the fields of aerospace and the like.
The magnesium or magnesium alloy is compounded with the negative thermal expansion material, so that the composite material has the mechanical property of metal and can reduce the CTE of the material, thereby prolonging the service life of the component.
At present, domestic researches on adjusting and controlling the CTE of the magnesium alloy are few, and the cost is mostly the loss of the original mechanical property. Meanwhile, the research on the magnesium alloy composite material with stronger mechanical property and lower CTE has not been reported at home and abroad.
Disclosure of Invention
The invention aims to solve the problems and provides a metal composite material with light weight, high strength and toughness and low thermal expansion coefficient and a preparation method thereof.
In order to achieve the purpose, the invention adopts the technical scheme that:
a preparation method of a light metal composite material with high strength and toughness and low thermal expansion coefficient comprises the following steps:
firstly, preparing negative thermal expansion material Mn x CoGe, wherein x is 0.9 ≦ x ≦ 1, preferably x ≦ 0.98;
secondly, obtaining Mn by sintering x CoGe/AZ91D composite material
1) The negative thermal expansion material Mn prepared in the step one x Mixing CoGe and metal matrix powder in proportion, fully grinding until the powder is uniformly mixed to obtain Mn x CoGe/AZ91D mixed powder, negative thermal expansion material Mn x The mass ratio of the CoGe to the metal matrix powder is 3-7: 93-97; the metal matrix is pure magnesium or magnesium alloy, or pure aluminum and alloy thereof;
2) mn obtained in the step 1) x Placing the CoGe/AZ91D mixed powder into a mold, vacuumizing the mold in a hot-pressing sintering furnace, heating the mold from room temperature to 500-600 ℃ at a heating rate of 15-25 ℃/min, pressurizing the mold to 23-27 MPa at the same time, keeping the temperature and the pressure for 50-70 minutes, and finally cooling the mold to room temperature along with the furnace to obtain Mn x CoGe/AZ91D composite material.
In the step 1) of the second step, the negative thermal expansion material Mn prepared in the step one x Putting the CoGe and the metal matrix powder into a planetary ball mill in proportion for ball milling for 2-3 h at a ball-to-material ratio of 8-12: 1 at a rotating speed of 70-90 r/min to obtain Mn x CoGe/AZ91D mixed powder.
Preferably, in the step 1) of the second step, the negative thermal expansion material Mn prepared in the first step is added x Ball milling CoGe and metal matrix powder in a planetary ball mill at a ball-to-material ratio of 10: 1 for 2.5 hr at 80r/min to obtain Mn x CoGe/AZ91D mixed powder.
Preferably, the negative thermal expansion material Mn x The mass ratio of CoGe to metal matrix powder was 7: 93.
Preferably, in step 2) of step two, the Mn obtained in step 1) is added x Loading the CoGe/AZ91D mixed powder into a graphite die, and vacuumizing to 1 × 10 in a hot-pressing sintering furnace -5 Pa, raising the temperature from room temperature to 550 ℃ at the temperature rise rate of 20 ℃/min, simultaneously pressurizing to 25MPa, keeping the temperature and the pressure for 1h, and finally cooling to the room temperature along with the furnace to obtain Mn x CoGe/AZ91D composite materialAnd (5) feeding.
Preferably, the negative thermal expansion material Mn is prepared by adopting a solid-phase reaction method x CoGe, comprising the following steps:
1) weighing Mn powder, Co powder and Ge powder according to a molar ratio, and uniformly mixing;
2) grinding the powder mixed in the step 1) for 2 hours to ensure that the powder is uniformly mixed;
3) putting the powder obtained in the step 2) into a mold, pressing into blocks under 50Mpa, putting into a quartz tube, vacuumizing, and sealing the tube;
4) sintering the tube sealing sample obtained in the step 3) at 750 ℃ for 72h, and then cooling to room temperature along with the furnace;
5) taking out the tube sealing sample obtained in the step 4), preparing the tube sealing sample into powder, putting the powder into a ball mill for ball milling for 5 hours at the rotating speed of 250r/min and the ball-material ratio of 10: 1, and obtaining the negative thermal expansion material Mn x CoGe。
Preferably, the metal matrix is a magnesium alloy.
Further preferably, the magnesium alloy is AZ 91D.
A light-weight high-toughness low-thermal-expansion-coefficient metal composite material is prepared from Mn as negative thermal expansion material x CoGe and metal matrix powder are mixed and sintered in a hot pressing mode, and the negative thermal expansion material Mn x CoGe, 0.9. ltoreq. x.ltoreq.1, preferably 0.98; negative thermal expansion material Mn x The mass ratio of the CoGe to the metal matrix powder is 3-7: 93-97.
The light-weight, high-strength and high-toughness and low-thermal expansion coefficient metal composite material is prepared by any one of the preparation methods.
The invention has the beneficial effects that:
the method has the advantages of simple operation, excellent performance and high purity of the obtained negative thermal expansion material, and can be used for industrial production in batches.
The invention adopts metal or alloy thereof as a base material and a negative thermal expansion material MnCoGe as a reinforcing material, which not only can obviously reduce the thermal expansion coefficient of the metal base, but also has excellent mechanical properties of the metal. The aluminum, magnesium and alloy thereof can be selected as the substrate, and the obtained composite material has the characteristics of light weight, simple preparation method, low price and wide application range.
Drawings
FIG. 1 shows a negative thermal expansion material Mn prepared in example 1 of the present invention 0.98 And (4) X-ray diffraction analysis results of CoGe.
FIG. 2 shows Mn as a negative thermal expansion material prepared in example 1 of the present invention 0.98 Scanning electron microscope pictures of CoGe.
FIG. 3 shows Mn as a negative thermal expansion material prepared in example 1 of the present invention 0.98 Graph of the thermal expansion of CoGe, wherein, graph a is the linear thermal expansion curve of the material in the range from room temperature to 200 ℃, and graph b is the linear thermal expansion curve in the range from 74 ℃ to 77 ℃.
FIG. 4 shows Mn prepared in examples 1 to 3 of the present invention 0.98 And (3) the X-ray diffraction analysis result of the CoGe/AZ91D composite material.
FIG. 5 shows Mn prepared in examples 1 to 3 of the present invention 0.98 Gold phase diagram of CoGe/AZ91D composite material.
FIG. 6 shows Mn prepared in examples 1 to 3 of the present invention 0.98 Thermal expansion profile of CoGe/AZ91D composite.
FIG. 7 shows Mn prepared in examples 1 to 3 of the present invention 0.98 Compression performance graph of CoGe/AZ91D composite.
Detailed Description
The present invention will be described in detail with reference to specific examples. The following examples will assist those skilled in the art in further understanding the invention, but are not intended to limit the invention in any way. It should be noted that variations and modifications can be made by persons skilled in the art without departing from the spirit of the invention. All falling within the scope of the present invention.
The experimental methods in the following examples are all conventional methods unless otherwise specified; the reagents and materials used, unless otherwise specified, are conventional in the art and are commercially available.
Example 1
Negative thermal expansion material Mn 0.98 Preparation of CoGe: firstly, weighing Mn powder (with the purity of 99.98 percent), Co powder (with the purity of 99.99 percent) and Ge powder (with the purity of 99.9999 percent) according to a molar ratio, wherein the Mn powder is excessive by 1 percent and is ground in an agate mortar for 2 hours, so as to ensure that the powders are uniformly mixed. And (3) putting the powder into a die, applying a pressure of 50MPa to the powder by using a universal testing machine for forming, then putting the powder into a quartz tube, vacuumizing and sealing the quartz tube. Sintering in a box furnace at 750 deg.C for 72h, cooling to room temperature, taking out sample, filing into powder, ball milling in a planetary ball mill at 250r/min at ball material ratio of 10: 1 to obtain the negative thermal expansion material Mn 0.98 CoGe, for standby.
Adding Mn as negative thermal expansion material 0.98 Mixing CoGe according to the mass fraction of 3% with a metal matrix (magnesium alloy AZ91D powder with the purity of 99.9%), putting the mixed powder into a planetary ball mill for ball milling for 2.5h at the rotating speed of 80r/min and the ball-to-material ratio of 10: 1 to obtain Mn 0.98 CoGe/AZ91D mixed powder; wherein, the metal matrix can also be pure magnesium or other magnesium alloys, or aluminum and its alloys. Putting the uniformly mixed powder into a hot-pressing sintering furnace, and vacuumizing to 1 × 10 -5 Pa, raising the temperature from room temperature to 550 ℃ at the speed of 20 ℃/min, simultaneously pressurizing to 25MPa, keeping the temperature and the pressure for 1h, and finally cooling to the room temperature along with the furnace to obtain 3% -Mn 0.98 CoGe/AZ91D composite material.
Example 2
Negative thermal expansion material Mn 0.98 Preparation of CoGe: firstly, weighing Mn powder (with the purity of 99.98%), Co powder (with the purity of 99.99%) and Ge powder (with the purity of 99.9999%) according to a molar ratio, wherein the Mn powder is excessive by 1%, and grinding the Mn powder in an agate mortar for 2 hours to ensure that the powders are uniformly mixed. And putting the powder into a die, applying a pressure of 50MPa to the powder by using a universal tester for forming, then putting the powder into a quartz tube, vacuumizing and sealing the quartz tube. Sintering in a box furnace at 750 deg.C for 72h, cooling to room temperature, taking out sample, filing into powder, ball milling in a planetary ball mill at 250r/min for 5h at a ball-to-material ratio of 10: 1 to obtain the material Mn 0.98 CoGe, for standby.
Adding Mn as negative thermal expansion material 0.98 CoGe in a mass fraction of 5% andmixing metal matrix (AZ 91D powder with purity of 99.9%), ball milling in a planetary ball mill for 2.5 hr at 80r/min at a ball-to-material ratio of 10: 1 to obtain Mn 0.98 CoGe/AZ91D mixed powder; wherein, the metal matrix can also be pure magnesium or other magnesium alloys, or aluminum and its alloys. Putting the uniformly mixed powder into a hot-pressing sintering furnace, and vacuumizing to 1 × 10 -5 Pa, raising the temperature from room temperature to 550 ℃ at the speed of 20 ℃/min, simultaneously pressurizing to 25MPa, keeping the temperature and the pressure for 1h, and finally cooling to the room temperature along with the furnace to obtain 5% -Mn 0.98 CoGe/AZ91D composite material.
Example 3
Negative thermal expansion material Mn 0.98 Preparation of CoGe: firstly, weighing Mn powder (with the purity of 99.98 percent), Co powder (with the purity of 99.99 percent) and Ge powder (with the purity of 99.9999 percent) according to a molar ratio, wherein the Mn powder is excessive by 1 percent and is ground in an agate mortar for 2 hours, so as to ensure that the powders are uniformly mixed. And putting the powder into a die, applying a pressure of 50MPa to the powder by using a universal tester for forming, then putting the powder into a quartz tube, vacuumizing and sealing the quartz tube. Sintering in a box furnace at 750 deg.C for 72h, cooling to room temperature, taking out sample, filing into powder, ball milling in a planetary ball mill at 250r/min for 5h at a ball-to-material ratio of 10: 1 to obtain the material Mn 0.98 CoGe, for standby.
Adding Mn as negative thermal expansion material 0.98 Mixing CoGe according to the mass fraction of 7% with a metal matrix (AZ 91D powder with the purity of 99.9%), putting the mixed powder into a planetary ball mill for ball milling for 2.5h at the rotating speed of 80r/min and the ball-to-material ratio of 10: 1 to obtain Mn 0.98 CoGe/AZ91D mixed powder; wherein, the metal matrix can also be pure magnesium or other magnesium alloys, or aluminum and its alloys. Putting the uniformly mixed powder into a hot-pressing sintering furnace, and vacuumizing to 1 × 10 -5 Pa, raising the temperature from room temperature to 550 ℃ at the speed of 20 ℃/min, simultaneously pressurizing to 25MPa, keeping the temperature and the pressure for 1h, and finally cooling to the room temperature along with the furnace to obtain 7% -Mn 0.98 CoGe/AZ91D composite material.
Example 4
Product detection
One, negative thermal expansion materialMn Material 0.98 CoGe
The negative thermal expansion material prepared in example 1 was analyzed by X-ray diffraction and observed by scanning electron microscopy, and the results are shown in FIGS. 1 and 2, respectively, and it can be seen from FIG. 1 that the obtained negative thermal expansion material and Mn 0.98 The diffraction peak matching of the CoGe standard PDF card is good, and the prepared material can be determined to be a negative thermal expansion material Mn 0.98 CoGe. From FIG. 2, it can be seen that Mn is produced 0.98 The CoGe powder had a small average particle size, with the majority of the particles being about 1 μm in size.
The thermal expansion curves are plotted, fig. 3a is a thermal expansion coefficient curve of the prepared negative thermal expansion material ranging from room temperature to 200 c, and fig. 3b is a linear thermal expansion curve ranging from 74 to 77 c. It can be seen from fig. 3a that the linear thermal expansion coefficient α is 9.83 × 10 in the temperature range from room temperature to 200 ℃ -6 ℃ -1 And less than half of the thermal expansion coefficient of the common magnesium alloy. A sharp drop in the curve can be seen, indicating the occurrence of negative thermal expansion. FIG. 3b is a linear fit of the curve of the thermal expansion coefficient with the abscissa ranging from 74 ℃ to 77 ℃ to obtain the negative thermal expansion material Mn in the temperature range 0.98 Coefficient of linear thermal expansion of CoGe ═ 154.2X 10 -6 ℃ -1 。
II, Mn 0.98 CoGe/AZ91D composite material
(1) X-ray diffraction analysis
For Mn prepared in examples 1 to 3 0.98 X-ray diffraction analysis of the CoGe/AZ91D composite material revealed that Mn is present in Mn as shown in FIG. 4 0.98 At a CoGe content of 0%, only the diffraction peak of Mg is present, while with Mn 0.98 Addition of CoGe, Mn 0.98 The CoGe phase was detected. In addition, due to Mn 0.98 CoGe reacts with the substrate, Mg is present 2 Diffraction peak of Ge.
(2) Golden photo picture
FIG. 5 shows Mn prepared in examples 1 to 3 0.98 Gold phase diagram of CoGe/AZ91D composite material, FIG. 5a is without Mn addition 0.98 AZ91D material control for CoGe, FIGS. 5b, 5c, 5d correspond to Mn produced in examples 1, 2, 3, respectively 0.98 CoGe/AZ91D composite material. As can be seen from the view of figure 5,obtained 3% -Mn 0.98 The CoGe/AZ91D composite material has obvious crystal grains, the average crystal grain size is 50 mu m, and a small amount of precipitated phases are generated among the crystal grains; obtained 5% -Mn 0.98 The CoGe/AZ91D composite material has more obvious crystal grains and a intergranular precipitated phase which is compared with 3% -Mn 0.98 More CoGe/AZ91D composite material; obtained 7% -Mn 0.98 The CoGe/AZ91D composite material has more obvious crystal grains and a more intergranular precipitated phase than 5% -Mn 0.98 The CoGe/AZ91D composite material is more.
(3) Graph of thermal expansion
The Mn prepared in examples 1 to 3 is plotted 0.98 Thermal expansion profile of CoGe/AZ91D composite, as shown in FIG. 6: obtained 3% -Mn 0.98 The coefficient of thermal expansion of the CoGe/AZ91D composite material is 25.3 multiplied by 10 -6 ℃ -1 Compared with 25.7 multiplied by 10 of the metal matrix -6 ℃ -1 Slightly reduced; obtained 5% -Mn 0.98 The coefficient of thermal expansion of the CoGe/AZ91D composite material is 24.5 multiplied by 10 -6 ℃ -1 Is reduced by 1.2X 10 compared with the metal matrix -6 ℃ -1 (ii) a Obtained 7% -Mn 0.98 The coefficient of thermal expansion of the CoGe/AZ91D composite material is 17.7 multiplied by 10 -6 ℃ -1 Compared with a metal matrix, the reduction rate is reduced by 31 percent, and the reduction effect is obvious.
(4) Compression performance curve diagram
The Mn prepared in examples 1 to 3 is plotted 0.98 The compressive performance graph of the CoGe/AZ91D composite material is shown in FIG. 7:
obtained 3% -Mn 0.98 The compressive yield strength of the CoGe/AZ91D composite material is 110Mpa, which is slightly reduced compared with 119Mpa of a metal matrix; the ultimate compressive strength is 410Mpa, which is equivalent to 411Mpa of the metal matrix; the elongation was 28.6%, which corresponds to 28.5% of the metal matrix.
Obtained 5% -Mn 0.98 The compressive yield strength of the CoGe/AZ91D composite material is 121MPa, which is slightly improved compared with 119MPa of a metal matrix; the ultimate compressive strength is 428Mpa, which is increased by 17Mpa compared with 411Mpa of the metal matrix; the elongation was 26.1%, which was slightly lower than 28.5% of the metal matrix.
Obtained 7% -Mn 0.98 The CoGe/AZ91D composite material has a compressive yield strength of157Mpa, which is 31.9 percent higher than 119Mpa of the metal matrix; the ultimate compressive strength is 412Mpa, which is equivalent to 411Mpa of the metal matrix; the elongation was 26%, which was slightly lower than 28.5% of the metal matrix.
Claims (10)
1. A preparation method of a light metal composite material with high strength and toughness and low thermal expansion coefficient is characterized by comprising the following steps:
firstly, preparing a negative thermal expansion material Mn x CoGe, wherein x is 0.9 ≦ x ≦ 1, preferably x ≦ 0.98;
secondly, obtaining Mn by sintering x CoGe/AZ91D composite material
1) The negative thermal expansion material Mn prepared in the step one x Mixing CoGe and metal matrix powder in proportion, and fully grinding until the powder is uniformly mixed to obtain Mn x CoGe/AZ91D mixed powder, negative thermal expansion material Mn x The mass ratio of the CoGe to the metal matrix powder is 3-7: 93-97; the metal matrix is pure magnesium or magnesium alloy, or pure aluminum and alloy thereof;
2) mn obtained in the step 1) x Placing the CoGe/AZ91D mixed powder into a mold, vacuumizing the mold in a hot-pressing sintering furnace, heating the mold from room temperature to 500-600 ℃ at a heating rate of 15-25 ℃/min, pressurizing the mold to 23-27 MPa at the same time, keeping the temperature and the pressure for 50-70 minutes, and finally cooling the mold to room temperature along with the furnace to obtain Mn x CoGe/AZ91D composite material.
2. The method of claim 1, wherein: in the step 1) of the second step, the negative thermal expansion material Mn prepared in the step one x Putting the CoGe and the metal matrix powder into a planetary ball mill in proportion for ball milling for 2-3 h at a ball-to-material ratio of 8-12: 1 at a rotating speed of 70-90 r/min to obtain Mn x CoGe/AZ91D mixed powder.
3. The method of claim 2, wherein: in the step 1) of the second step, the negative thermal expansion material Mn prepared in the step one x Placing CoGe and metal matrix powder into a planetary ball mill in proportion for ball milling, wherein the ball-to-material ratio is10: 1, ball milling for 2.5h at the rotating speed of 80r/min to obtain Mn x CoGe/AZ91D mixed powder.
4. The method of claim 1, wherein: negative thermal expansion material Mn x The mass ratio of CoGe to metal matrix powder was 7: 93.
5. The method of claim 1, wherein: in step 2) of step two, Mn obtained in step 1) is added x Loading the CoGe/AZ91D mixed powder into a graphite die, and vacuumizing to 1 × 10 in a hot-pressing sintering furnace -5 Pa, raising the temperature from room temperature to 550 ℃ at the temperature rise rate of 20 ℃/min, simultaneously pressurizing to 25MPa, keeping the temperature and the pressure for 1h, and finally cooling to the room temperature along with the furnace to obtain Mn x CoGe/AZ91D composite material.
6. The method of claim 1, wherein: preparation of negative thermal expansion material Mn by solid phase reaction method x CoGe, comprising the following steps:
1) weighing Mn powder, Co powder and Ge powder according to a molar ratio, and uniformly mixing;
2) grinding the powder mixed in the step 1) for 2 hours to ensure that the powder is uniformly mixed;
3) putting the powder obtained in the step 2) into a mold, pressing into blocks under 50Mpa, putting into a quartz tube, vacuumizing, and sealing the tube;
4) sintering the tube sealing sample obtained in the step 3) at 750 ℃ for 72h, and then cooling to room temperature along with the furnace;
5) taking out the tube sealing sample obtained in the step 4), preparing the tube sealing sample into powder, putting the powder into a ball mill for ball milling for 5 hours at the rotating speed of 250r/min and the ball material ratio of 10: 1, and obtaining the negative thermal expansion material Mn x CoGe。
7. The production method according to any one of claims 1 to 6, characterized in that: the metal matrix is magnesium alloy.
8. The method of claim 7, wherein: the magnesium alloy is AZ 91D.
9. A light, high-strength and high-toughness and low-thermal expansion coefficient metal composite material is characterized in that: adopting a negative thermal expansion material Mn x CoGe and metal matrix powder are mixed and sintered in a hot pressing mode, and the negative thermal expansion material Mn x CoGe, 0.9. ltoreq. x.ltoreq.1, preferably 0.98; negative thermal expansion material Mn x The mass ratio of the CoGe to the metal matrix powder is 3-7: 93-97.
10. The metallic composite of claim 9, wherein: obtained by the production method according to any one of claims 1 to 8.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210049620.9A CN114959330B (en) | 2022-01-17 | 2022-01-17 | Light metal composite material with high strength and toughness and low thermal expansion coefficient and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210049620.9A CN114959330B (en) | 2022-01-17 | 2022-01-17 | Light metal composite material with high strength and toughness and low thermal expansion coefficient and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN114959330A true CN114959330A (en) | 2022-08-30 |
| CN114959330B CN114959330B (en) | 2022-12-02 |
Family
ID=82974367
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210049620.9A Active CN114959330B (en) | 2022-01-17 | 2022-01-17 | Light metal composite material with high strength and toughness and low thermal expansion coefficient and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN114959330B (en) |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106244835A (en) * | 2016-08-22 | 2016-12-21 | 中国科学院合肥物质科学研究院 | A kind of room temperature huge negative thermal expansion material of width warm area and preparation method thereof |
| CN111266587A (en) * | 2019-12-27 | 2020-06-12 | 上海交通大学 | Preparation method of light compact near-zero expansion metal matrix composite material |
-
2022
- 2022-01-17 CN CN202210049620.9A patent/CN114959330B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106244835A (en) * | 2016-08-22 | 2016-12-21 | 中国科学院合肥物质科学研究院 | A kind of room temperature huge negative thermal expansion material of width warm area and preparation method thereof |
| CN111266587A (en) * | 2019-12-27 | 2020-06-12 | 上海交通大学 | Preparation method of light compact near-zero expansion metal matrix composite material |
Also Published As
| Publication number | Publication date |
|---|---|
| CN114959330B (en) | 2022-12-02 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US11731178B2 (en) | Rolled (FeCoNiCrRn/Al)-2024Al composite panel and fabrication method thereof | |
| CN109295336B (en) | Preparation method of titanium-silicon alloy phase reinforced TiAl-based composite material with network structure | |
| CN108060341B (en) | A kind of high tenacity Ni50Mn25Ga25Memorial alloy and preparation method thereof | |
| CN110273092A (en) | A kind of CoCrNi particle reinforced magnesium base compound material and preparation method thereof | |
| CN114645180B (en) | Double-phase reinforced aluminum alloy and preparation method thereof | |
| CN110747380A (en) | Nano ceramic particle reinforced aluminum matrix composite material and preparation method thereof | |
| CN107513651B (en) | A kind of preparation method of titanium particle reinforced magnesium base composite material | |
| CN109868381B (en) | Preparation method of high-volume-fraction tungsten particle reinforced aluminum matrix composite material | |
| CN115433011A (en) | High-entropy carbide (VNbTaMoW) C 5 -SiC complex phase ceramics | |
| CN113213960B (en) | High-toughness and high-hardness wear-resistant ceramic and preparation method thereof | |
| CN114959330B (en) | Light metal composite material with high strength and toughness and low thermal expansion coefficient and preparation method thereof | |
| Wananuruksawong et al. | High-strain-rate superplasticity in nanocrystalline silicon nitride ceramics under compression | |
| CL et al. | Synthesis of Nb/Nb5Si3 in-situ composites by mechanical milling and reactive spark plasma sintering | |
| CN112011717A (en) | High-strength low-expansion composite material and preparation method thereof | |
| CL et al. | Microstructures and mechanical properties of Nb/Nb-silicide in-situ composites synthesized by reactive hot pressing of ball milled powders | |
| Mahesh et al. | Development and characterization of titanium nitride reinforced aluminium MMC’s through powder metallurgy technique | |
| CN113957294A (en) | CrCoNi intermediate entropy alloy reinforced Al-based composite material and preparation method thereof | |
| US3821005A (en) | Densification of silicon nitride | |
| CN113149658A (en) | Titanium nitride-based composite ceramic material and preparation method thereof | |
| US5887241A (en) | Method of manufacture of low O2 content MoSi2 /SiC composite bodies | |
| Peng et al. | Synthesis and mechanical properties of ternary molybdenum carbosilicide and its composite | |
| Wang et al. | Micrometer-sized titanium carbide with properties comparable to those of nanocrystalline counterparts | |
| CN110256085B (en) | Preparation method of tough and wear-resistant silicon nitride-based composite ceramic | |
| CN116144968B (en) | Ti with excellent room temperature plasticity2Preparation method of AlNb-based composite material | |
| Nieh et al. | Creep of a niobium beryllide, Nb2Be17 |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |