CN110578082A - High-strength high-thermal-conductivity iron-based alloy and preparation method thereof - Google Patents

High-strength high-thermal-conductivity iron-based alloy and preparation method thereof Download PDF

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CN110578082A
CN110578082A CN201910536735.9A CN201910536735A CN110578082A CN 110578082 A CN110578082 A CN 110578082A CN 201910536735 A CN201910536735 A CN 201910536735A CN 110578082 A CN110578082 A CN 110578082A
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powder
nial
iron
steps
ball milling
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白亚平
李建平
杨忠
成超
周瑾
王刚
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Shandong Dachai Cylinder Block & Cylinder Head Co Ltd
Xian Technological University
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Shandong Dachai Cylinder Block & Cylinder Head Co Ltd
Xian Technological University
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    • 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
    • C22C1/05—Mixtures of metal powder with non-metallic powder
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0068—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only nitrides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0292—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with more than 5% preformed carbides, nitrides or borides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel

Abstract

The invention relates to a high-strength high-thermal conductivity iron-based alloy and a preparation method thereof, which comprises the steps of firstly, proportioning Ni powder and Al powder in a ratio of 1:1, carrying out ball milling to obtain fine and uniform nano NiAl powder with a B2 structure, then continuously carrying out ball milling and mixing on the prepared NiAl powder, Fe powder and AlN powder to obtain alloy powder, and finally carrying out hot-pressing sintering on the alloy powder to form a required block composite material; the invention combines the mechanical alloying technology and the hot-pressing sintering technology, the preparation method is simple, the preparation method can reduce the overall density of the iron-based material, simultaneously improve the mechanical property and the thermal conductivity of the iron-based material, and the obtained product has low cost, high purity, low density and excellent mechanical property and thermophysical property.

Description

high-strength high-thermal-conductivity iron-based alloy and preparation method thereof
Technical Field
the invention belongs to the technical field of iron-based alloys, and particularly relates to a high-strength high-thermal-conductivity iron-based alloy and a preparation method thereof.
Background
Compared with gasoline engine, diesel engine has the features of high power, high heat efficiency, high maximum explosion pressure, etc. The working conditions are worse, and the cylinder head is an important part of the engine and forms a combustion space together with the piston, so the strength requirement of the cylinder head is higher. In order to meet the strength requirement, the cylinder head of the diesel engine is generally made of cast iron materials instead of cast aluminum materials. With the requirement of light weight of equipment and the further improvement of power density of a diesel engine, the traditional cylinder cover material cannot meet the use requirement, so that the development of a light high-strength high-heat-conductivity iron-based alloy new material is a great importance.
In CN 108588530 a, such technical information is disclosed that artificial diamond powder subjected to surface treatment can be added as a reinforcing phase to an iron-based alloy, thereby greatly improving the thermal conductivity of the material while reducing the overall material density, but researches show that the addition is not obvious in improving the overall mechanical properties of the material, and the mechanical properties of the material cannot meet the use requirements.
Disclosure of Invention
The invention aims to provide a high-strength high-thermal-conductivity iron-based alloy and a preparation method thereof, so as to solve the problem that the mechanical property of the material in the prior art is difficult to meet the use requirement.
A preparation method of a high-strength high-thermal-conductivity iron-based alloy comprises the following steps:
the method comprises the following steps: mixing Ni powder and Al powder according to an atomic ratio of 1:1, putting the mixture into a ball milling tank which is vacuumized and filled with argon gas for ball milling, and performing operation/stop interval time of 30min for 70h in total to obtain fine and uniform nano NiAl powder with a B2 structure;
Step two: 42.50-48.50 parts of Fe powder and 42.50-48.50 parts of NiAl powder prepared in the first step, wherein the mass ratio of the NiAl powder to the Fe powder is 1:1, 3.00-15.00 parts of AlN powder are added, and the mixture is continuously subjected to ball milling and mixing for 5 hours to obtain final alloy powder, wherein the total of the Fe powder, the NiAl powder and the AlN powder is 100 parts;
Step three: and filling the alloy powder obtained in the step two into a graphite die, and performing hot-pressing sintering to form the required block composite material, wherein the sintering temperature is 1050 ℃, and the sintering pressure is 20 MPa.
in the first step, a step-by-step ball milling method is adopted, the mass ratio of the materials to the milling balls is 1:10, the rotating speed is 250r/min, and the particle size of the prepared powder is 100nm-200 nm.
in the second step, a step-by-step ball milling method is adopted, the mass ratio of the materials to the milling balls is 1:3, and the rotating speed is 100 r/min.
in the third step, the technological parameters of hot-pressing sintering are as follows: vacuum degree of 6.67X 10-3And Pa, heating the hot-pressed sintering to the target temperature 1050 ℃ at the heating rate of 10 ℃/min, preserving the heat for 60min, and then cooling to the room temperature along with the furnace.
the iron-based alloy with high strength and high thermal conductivity prepared by the preparation method.
Compared with the prior art, the invention has the beneficial effects that:
1. The preparation method is simple, and the mass fraction of AlN in the AlN/NiAl reinforced Fe-based alloy is adjusted according to the addition of AlN powder in the mechanical alloying process, so that the density of the material is reduced, and the mechanical property and the high-temperature thermophysical property of the material are improved;
2. The mechanical alloying technology is combined with the hot-pressing sintering technology, and the developed novel AlN/NiAl reinforced iron-based alloy can be applied to the technical fields of high-power-density diesel engine cylinder head materials and the like.
3. The theoretical density of the aluminum nitride is 3.26g/cm3The crystal structure of the material is similar to that of diamond, the hardness and the strength of the material are high at room temperature and high temperature, the material has good high-temperature corrosion resistance and low cost, and the material has good wettability with an iron matrix and a NiAl phase with a B2 structure, does not have poor interface reaction and has good physical and chemical compatibility. Therefore, the double addition of the dispersed aluminum nitride and the NiAl phase with the B2 structure is expected to reduce the iron-based materialThe whole density is improved, and the mechanical property is improved, and the thermal conductivity is improved.
4. The preparation process adopts a staged ball milling process, and the obtained product has low cost, high purity, low density and excellent mechanical property and thermophysical property.
Drawings
FIG. 1 is SEM topography and XRD phase analysis of mechanically alloyed NiAl powder;
FIG. 2 is a TEM analysis of a 5.00wt.% AlN-reinforced NiAl/Fe alloy of example 2;
FIG. 3 is the SEM and point analysis results of 10.00wt.% AlN reinforced NiAl/Fe alloy block composite after hot pressing and sintering in example 3.
Detailed Description
The present invention will be described in further detail with reference to specific examples, but the embodiments of the present invention include, but are not limited to, the scope shown in the following examples.
The invention relates to a preparation method of AlN/NiAl reinforced iron-based alloy with high strength and high thermal conductivity, which adopts Ni powder and Al powder to react in the mechanical alloying process to generate NiAl powder particles with a nano B2 ordered structure, then NiAl powder, AlN powder and Fe powder with a B2 structure are continuously and uniformly mixed according to a certain proportion to obtain fine and uniform AlN/NiAl reinforced iron-based alloy composite powder, and then hot-press sintering is carried out to obtain a block composite material so as to obtain a low-density heat-resistant AlN/NiAl reinforced Fe-based material.
the method comprises the following steps:
The method comprises the following steps: according to the material: grinding ball = 1:10, proportioning Ni powder and Al powder according to the atomic ratio of 1:1, putting the mixture into a ball-milling tank which is vacuumized and filled with argon, and carrying out ball milling at the rotating speed of 250r/min, wherein the running/stopping interval time is 30min, and the total time is 70h, so that the fine and uniform nano NiAl powder with the B2 structure is obtained.
Step two: weighing 42.50-48.50% of Fe powder, 42.50-48.50% of NiAl powder with a nanoscale B2 structure and 3.00-15.00% of AlN powder according to mass fraction; and (2) proportioning Fe powder and NiAl powder with a B2 structure according to the mass percent of 1:1, adding AlN powder with the mass percent of 3.00-15.00%, and continuously mixing for 5 hours in a ball mill with the ball-material ratio of 3:1 and the rotating speed of 100r/min to obtain the final alloy powder.
Step three: filling the alloy powder obtained in the third step into a graphite die, and forming the required block composite material by hot-pressing sintering; wherein the sintering temperature is 1050 ℃, and the sintering pressure is 20 MPa.
Example 1:
Putting Ni powder (20.55g) and Al powder (9.45g) into a zirconium dioxide ball-milling tank according to the atomic ratio of raw materials of 1:1, adding 300g of zirconium dioxide grinding balls with the diameter of 10mm, vacuumizing the ball-milling tank and filling argon after sealing by an O-shaped sealing ring before ball-milling, carrying out ball-milling at the rotating speed of 250r/min for 30min at the operation/stop interval time, and carrying out mixed ball-milling for 70h in total to obtain the fine and uniform nano NiAl powder with the B2 structure. FIG. 1 is an SEM photograph and an XRD spectrum of 1NiAl powder. As can be seen from FIG. 1, the NiAl powder is relatively fine, the particle surface is relatively round, and the particle size of the powder is about 100-200 nm. The stronger diffraction peaks appearing in the XRD spectrogram of FIG. 1 (B) are the diffraction peaks of the (100), (110) and (211) planes, which are both the diffraction peaks of NiAl with the structure of intermetallic compound B2, and show that NiAl powder with the structure of B2 can be successfully prepared by mechanical alloying.
Step two, according to the mass fraction of the raw materials: 48.50% of Fe powder (48.50g), 48.50% of AlN powder (48.50g) and 3.00% of NiAl (3.00g) powder prepared in the steps are put into a stainless steel ball milling tank, the grinding balls are stainless steel grinding balls, and the stainless steel grinding balls are mixed for 5 hours in a ball mill with the ball-material ratio of 3:1 and the rotating speed of 100r/min, so that 3.00% of AlN/NiAl reinforced Fe-based composite powder is obtained.
And step three, weighing 30g of the mixture powder, filling the mixture powder into a high-strength graphite die, and sintering the mixture powder in a hot-pressing sintering furnace (ZT-40-20Y) produced by Shanghai Chenghua electric furnace Limited company. The main sintering process parameters are as follows: the degree of vacuum was 6.67X 10-3And Pa, heating the hot-pressed sintered body to 1050 ℃ at the heating rate of 10 ℃/min, preserving the heat for 60min, and then cooling the sintered body to room temperature along with the furnace to finally obtain the AlN/NiAl reinforced Fe-based alloy sintered body with the mass fraction of 3.00 percent.
the sintered body is machined to a certain size by mechanical cutting, and according to the specific operation of experimental polishing, firstly, the sintered body is polished on sand paper, and then polished on a polishing machinethe density, hardness, room temperature compressive strength and 500 ℃ high temperature thermal conductivity of the material are tested, and the results are as follows: the density was measured to be 6.25g/cm3Compared with pure iron, the iron content is reduced by 17.00%; the hardness is 47.00HRC, the room-temperature compressive strength is 2150.30MPa, and the hardness is improved by 188.55 percent compared with pure iron; the high-temperature thermal conductivity coefficient is 31.93W/(m.K), which is improved by 2.87 percent compared with pure iron.
Note: pure iron prepared by the same hot-pressing sintering process was used as a reference material for comparison, as follows.
Example 2:
Putting Ni powder (20.55g) and Al powder (9.45g) into a zirconium dioxide ball-milling tank according to the atomic ratio of raw materials of 1:1, adding 300g of zirconium dioxide grinding balls with the diameter of 10mm, vacuumizing the ball-milling tank and filling argon after sealing by an O-shaped sealing ring before ball-milling, carrying out ball-milling at the rotating speed of 250r/min for 30min at the operation/stop interval time, and carrying out mixed ball-milling for 70h in total to obtain the fine and uniform nano NiAl powder with the B2 structure. FIG. 1 is an SEM photograph and an XRD spectrum of NiAl powder. As can be seen from FIG. 1, the NiAl powder is relatively fine, the particle surface is relatively round, and the particle size of the powder is about 100-200 nm. The stronger diffraction peaks appearing in the XRD spectrogram of FIG. 1 (B) are the diffraction peaks of the (100), (110) and (211) planes, which are both the diffraction peaks of NiAl with the structure of intermetallic compound B2, and show that NiAl powder with the structure of B2 can be successfully prepared by mechanical alloying.
Step two, according to the mass fraction of the raw materials: 47.50% of Fe powder (47.50g) and 47.50% of NiAl powder (47.50g) and 5.00% of AlN powder (5.00g) prepared in the steps are put into a stainless steel ball milling tank, the grinding balls are stainless steel grinding balls, and the stainless steel grinding balls are mixed for 5 hours in a ball mill with the ball-material ratio of 3:1 and the rotating speed of 100r/min, so that fine and uniform 5.00% of AlN/NiAl reinforced Fe-based composite powder is obtained.
and step three, weighing 30g of the mixture powder, filling the mixture powder into a high-strength graphite die, and sintering the mixture powder in a hot-pressing sintering furnace (ZT-40-20Y) produced by Shanghai Chenghua electric furnace Limited company. The specific sintering process was the same as in example 1. The specimens were cut and tested as in example 1.
The sintered body was mechanically cut into a sheet having a thickness of about 0.5mm, and then ground with sandpaper to a thickness of about 0.5mm<Cutting 50 μm thin sheet into 3mmThe small round piece is processed with pit, then the sample is further thinned by Gatan691 precise ion thinning instrument to meet the requirement of transmission sample, the microstructure appearance is observed by JEOL, JEM-2010 transmission electron microscope, fig. 2 is the TEM analysis result of the block composite material after the hot pressing sintering of the embodiment 2, the irregular block particles in the picture can be determined to be AlN by combining the (a) and (b) of fig. 2, the size difference of the AlN particles is larger, the 300 nm ~ 3.5.5 μm is unequal, the AlN particles and the matrix interface is enlarged and observed as shown in fig. 2 (b), the AlN particles and the matrix are tightly combined, the density is tested to be 6.14g/cm3Compared with pure iron, the iron content is reduced by 18.46%; the hardness is 59.50HRC, the room-temperature compressive strength is 2220.50MPa, and the hardness is 197.97% higher than that of pure iron; the high-temperature thermal conductivity coefficient is 33.19W/(m.K), which is improved by 6.86% compared with pure iron.
Example 3:
Putting Ni powder (20.55g) and Al powder (9.45g) into a zirconium dioxide ball-milling tank according to the atomic ratio of the raw materials of 1:1, adding 300g of zirconium dioxide milling balls with the diameter of 10mm, vacuumizing the ball-milling tank and filling argon after sealing by an O-shaped sealing ring before ball-milling, carrying out ball-milling at the rotating speed of 250r/min, carrying out operation/stop interval time of 30min, and carrying out mixed ball-milling for 70h in total to obtain the fine and uniform nano NiAl powder with the B2 structure. FIG. 1 is an SEM photograph and an XRD spectrum of NiAl powder. As can be seen from FIG. 1, the NiAl powder is relatively fine, the particle surface is relatively round, and the particle size of the powder is about 100-200 nm. The stronger diffraction peaks appearing in the XRD spectrogram of FIG. 1 (B) are the diffraction peaks of the (100), (110) and (211) planes, which are both the diffraction peaks of NiAl with the structure of intermetallic compound B2, and show that NiAl powder with the structure of B2 can be successfully prepared by mechanical alloying.
According to the mass fraction of the raw materials: 47.50% of Fe powder (47.50g) and 47.50% of NiAl powder (47.50g) and 10.00% of AlN powder (10.00g) which are prepared in the steps are put into a stainless steel ball milling tank, the grinding balls are stainless steel grinding balls, and the stainless steel grinding balls are mixed for 5 hours in a ball mill with the ball-material ratio of 3:1 and the rotating speed of 100r/min, so that fine and uniform 10.00% of AlN/NiAl reinforced Fe-based composite powder is obtained.
30g of the above mixture powder was weighed, charged into a high-strength graphite mold, and sintered in a hot-pressing sintering furnace (ZT-40-20Y) manufactured by Shanghai Chenghua electric furnace Co. The specific sintering process was the same as in example 1.
cutting a sample, grinding and polishing according to the method in the example 1, and observing the microstructure morphology of the processed sample by using a Hitachi5-2500 scanning electron microscope. FIG. 3 shows the results of the microscopic morphology and point analysis of the composite block obtained in example 3. As can be seen from FIG. 3, the black AlN particles are relatively uniformly dispersed in the NiAl/Fe alloy. The density was measured to be 5.82g/cm3Compared with pure iron, the iron content is reduced by 22.71%; the hardness is 55.30HRC, the room-temperature compressive strength is 2080.30MPa, and the hardness is improved by 179.16 percent compared with pure iron; the high-temperature thermal conductivity coefficient is 34.24W/(m.K), which is improved by 10.24% compared with pure iron.
Example 4:
Putting Ni powder (20.55g) and Al powder (9.45g) into a zirconium dioxide ball-milling tank according to the atomic ratio of the raw materials of 1:1, adding 300g of zirconium dioxide milling balls with the diameter of 10mm, vacuumizing the ball-milling tank and filling argon after sealing by an O-shaped sealing ring before ball-milling, carrying out ball-milling at the rotating speed of 250r/min, carrying out operation/stop interval time of 30min, and carrying out mixed ball-milling for 70h in total to obtain the fine and uniform nano NiAl powder with the B2 structure. FIG. 1 is an SEM photograph and an XRD spectrum of NiAl powder. As can be seen from FIG. 1, the NiAl powder is relatively fine, the particle surface is relatively round, and the particle size of the powder is about 100-200 nm. The stronger diffraction peaks appearing in the XRD spectrogram of FIG. 1 (B) are the diffraction peaks of the (100), (110) and (211) planes, which are both the diffraction peaks of NiAl with the structure of intermetallic compound B2, and show that NiAl powder with the structure of B2 can be successfully prepared by mechanical alloying.
According to the mass fraction of the raw materials: 42.50 percent of Fe powder (42.50g) and 42.50 percent of NiAl powder (42.50g) and 15.00 percent of AlN powder (15.00g) which are prepared in the steps are put into a stainless steel ball milling pot, the grinding balls are stainless steel grinding balls, and the stainless steel grinding balls are mixed for 5 hours in a ball mill with the ball-material ratio of 3:1 and the rotating speed of 100r/min to obtain fine and uniform 15.00 percent of AlN/NiAl reinforced Fe-based composite powder
30g of the above mixture powder was weighed, charged into a high-strength graphite mold, and sintered in a hot-pressing sintering furnace (ZT-40-20Y) manufactured by Shanghai Chenghua electric furnace Co. The specific sintering process was the same as in example 1. The specimens were cut and tested as in example 1 with the following results: the density was measured to be 5.24g/cm3Compared with pure iron, the iron content is reduced by 30.41%; the hardness is 46.00HRC, the room-temperature compressive strength is 1950.2MPa, and the hardness is improved by 161.70 percent compared with pure iron; the high-temperature thermal conductivity coefficient is 21.79W/(m.K), which is reduced compared with pure iron.
In the above embodiments, embodiment 3 is the most preferred embodiment.
The preparation method is simple, and the prepared iron-based alloy is low in density, high in hardness, high in compressive strength, excellent in comprehensive mechanical property and good in thermal conductivity.

Claims (4)

1. a preparation method of a high-strength high-thermal-conductivity iron-based alloy is characterized by comprising the following steps:
The method comprises the following steps:
The method comprises the following steps: mixing Ni powder and Al powder according to an atomic ratio of 1:1, putting the mixture into a ball milling tank which is vacuumized and filled with argon gas for ball milling, and performing operation/stop interval time of 30min for 70h in total to obtain fine and uniform nano NiAl powder with a B2 structure;
step two: 42.50-48.50 parts of Fe powder and 42.50-48.50 parts of NiAl powder prepared in the first step, wherein the mass ratio of the NiAl powder to the Fe powder is 1:1, 3.00-15.00 parts of AlN powder are added, and the mixture is continuously subjected to ball milling and mixing for 5 hours to obtain final alloy powder, wherein the total of the Fe powder, the NiAl powder and the AlN powder is 100 parts;
Step three: and filling the alloy powder obtained in the step two into a graphite die, and performing hot-pressing sintering to form the required block composite material, wherein the sintering temperature is 1050 ℃, and the sintering pressure is 20 MPa.
2. The method for preparing the iron-based alloy with high strength and high thermal conductivity according to claim 1, wherein the method comprises the following steps:
In the first step, a step-by-step ball milling method is adopted, the mass ratio of the materials to the milling balls is 1:10, the rotating speed is 250r/min, and the particle size of the prepared powder is 100nm-200 nm.
3. The method for preparing the iron-based alloy with high strength and high thermal conductivity according to claim 2, wherein the method comprises the following steps:
in the second step, a step-by-step ball milling method is adopted, the mass ratio of the materials to the milling balls is 1:3, and the rotating speed is 100 r/min.
4. the method for preparing the iron-based alloy with high strength and high thermal conductivity according to claim 3, wherein the method comprises the following steps:
In the third step, the technological parameters of the hot-pressing sintering are as follows: vacuum degree of 6.67X 10-3And Pa, heating the hot-pressed sintering to the target temperature 1050 ℃ at the heating rate of 10 ℃/min, preserving the heat for 60min, and then cooling to the room temperature along with the furnace.
CN201910536735.9A 2019-06-20 2019-06-20 High-strength high-thermal-conductivity iron-based alloy and preparation method thereof Pending CN110578082A (en)

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