CN113528926A - Oriented FeAl-based alloy and preparation method thereof - Google Patents
Oriented FeAl-based alloy and preparation method thereof Download PDFInfo
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- CN113528926A CN113528926A CN202110653471.2A CN202110653471A CN113528926A CN 113528926 A CN113528926 A CN 113528926A CN 202110653471 A CN202110653471 A CN 202110653471A CN 113528926 A CN113528926 A CN 113528926A
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 71
- 239000000956 alloy Substances 0.000 title claims abstract description 71
- 229910015372 FeAl Inorganic materials 0.000 title claims abstract description 67
- 238000002360 preparation method Methods 0.000 title claims abstract description 8
- 239000013078 crystal Substances 0.000 claims abstract description 20
- 238000007711 solidification Methods 0.000 claims abstract description 10
- 230000008023 solidification Effects 0.000 claims abstract description 10
- 238000000034 method Methods 0.000 claims abstract description 8
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 4
- 229910052802 copper Inorganic materials 0.000 claims abstract description 4
- 239000010949 copper Substances 0.000 claims abstract description 4
- 239000000203 mixture Substances 0.000 claims abstract description 3
- 230000008018 melting Effects 0.000 claims abstract 2
- 238000002844 melting Methods 0.000 claims abstract 2
- 238000003723 Smelting Methods 0.000 claims description 10
- 238000010438 heat treatment Methods 0.000 claims description 9
- 239000002994 raw material Substances 0.000 claims description 8
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 6
- 238000005266 casting Methods 0.000 claims description 4
- 241001062472 Stokellia anisodon Species 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 3
- 239000000725 suspension Substances 0.000 claims description 3
- 229910002056 binary alloy Inorganic materials 0.000 abstract description 3
- 238000010587 phase diagram Methods 0.000 abstract description 3
- 230000008569 process Effects 0.000 abstract description 2
- 238000001000 micrograph Methods 0.000 description 13
- 230000000052 comparative effect Effects 0.000 description 6
- 230000006835 compression Effects 0.000 description 5
- 238000007906 compression Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 229910052782 aluminium Inorganic materials 0.000 description 3
- 238000004321 preservation Methods 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 229910015370 FeAl2 Inorganic materials 0.000 description 1
- 238000004523 catalytic cracking Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000004043 dyeing Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000000879 optical micrograph Methods 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 230000035699 permeability Effects 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 230000007847 structural defect Effects 0.000 description 1
- 239000004753 textile Substances 0.000 description 1
- 230000008016 vaporization Effects 0.000 description 1
- 238000009834 vaporization Methods 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- 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
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B11/00—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B28/00—Production of homogeneous polycrystalline material with defined structure
- C30B28/04—Production of homogeneous polycrystalline material with defined structure from liquids
- C30B28/06—Production of homogeneous polycrystalline material with defined structure from liquids by normal freezing or freezing under temperature gradient
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
- C30B29/10—Inorganic compounds or compositions
- C30B29/52—Alloys
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- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
- C30B29/60—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape characterised by shape
- C30B29/605—Products containing multiple oriented crystallites, e.g. columnar crystallites
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Abstract
本发明公开了一种定向FeAl基合金的制备方法，所述的FeAl合金成分按原子百分比记为FeaAlb，其中37≤a≤45，55≤b≤63，a+b=100，其组织为柱状晶；其步骤为：根据FeAl二元合金体系相图选择合适成分；采用水冷铜坩埚和真空非自耗电弧熔炼炉制备圆柱棒母合金；采用Bridgman晶体生长装置对母合金棒进行定向凝固，得到所述具有定向柱状晶组织的FeAl基合金。对比等轴晶的FeAl基合金，本发明制备的定向FeAl基合金拥有更加优异的综合力学性能。
The invention discloses a preparation method of an oriented FeAl-based alloy. The FeAl alloy composition is recorded as Fe a Al b in atomic percentage, wherein 37≤a≤45, 55≤b≤63, a+b=100, and The structure is columnar crystal; the steps are: select appropriate components according to the phase diagram of the FeAl binary alloy system; use a water-cooled copper crucible and a vacuum non-consumable arc melting furnace to prepare a cylindrical rod master alloy; use a Bridgman crystal growth device to process the master alloy rod. Directional solidification is carried out to obtain the FeAl-based alloy with directional columnar crystal structure. Compared with the equiaxed FeAl-based alloy, the oriented FeAl-based alloy prepared by the present invention has more excellent comprehensive mechanical properties.
Description
Technical Field
The invention belongs to the technical field of directional solidification, and particularly relates to a preparation method of a directional FeAl-based alloy.
Background
FeAl alloy is one of the most promising aluminum-containing intermetallic compounds. Like other aluminum-containing alloys, FeAl alloy has the excellent characteristics of high specific strength, high thermal stability, corrosion resistance, oxidation resistance, good high-temperature mechanical properties and the like. In addition, because the high-temperature alloy takes two basic industrial elements of Fe and Al as main raw materials, compared with other high-temperature alloys, the high-temperature alloy has more advantages in cost and has great application potential in the aspects of high-temperature corrosion resistance, oxidation resistance, high-temperature structural materials and the like. Over the last twenty years, much progress has been made in the study of FeAl alloys. FeAl alloys have been successfully used in many applications, such as replacing FeCrAl heating elements for heating rods in textile dyeing machines; the thermocouple protective sleeve is used instead of stainless steel; a fluidized bed boiler bottom feed nozzle; a double-acting slide valve guide rail of the catalytic cracking device; heat exchange tubes and walls, etc. The FeAl alloy has high magnetic permeability and good wear resistance, and can be used as a magnetic head material.
Although the FeAl alloy has the advantages, the FeAl alloy has the defects of high brittleness, poor plasticity and toughness, low tensile strength and the like, so that the FeAl alloy is difficult to machine and form and is not suitable for important structural parts and high-precision complex parts. The specific reasons are as follows: the complex crystal structure and special atomic bond mode of FeAl alloy determine that the FeAl alloy has high elastic modulus and hardness, the performance of high-hardness materials is quite sensitive to the structure, and the tiny structural defects can cause brittle fracture of the materials. And defects in the material are usually formed on the grain boundaries, and the environmental hydrogen embrittlement also acts through the grain boundaries, where a vaporization reaction of hydrogen embrittlement occurs. Therefore, the brittleness of the FeAl alloy is mostly originated from the grain boundary, and the problem of brittleness of the intermetallic compound is solved by solving the brittleness problem of the grain boundary.
Disclosure of Invention
The invention aims to provide a preparation method of an oriented FeAl-based alloy.
The technical solution for realizing the purpose of the invention is as follows: preparation method of oriented FeAl-based alloy, wherein expression of oriented FeAl-based alloy is FeaAlbWherein a is more than or equal to 37 and less than or equal to 45, b is more than or equal to 55 and less than or equal to 63, and a + b =100, the method comprises the following steps:
(1) weighing raw materials according to the target FeAl alloy components;
(2) smelting and casting to obtain a FeAl alloy rod;
(3) under the protection of argon, a Bridgman crystal growth device is adopted to carry out directional solidification on the cylindrical rod alloy, the heating temperature is 1200-1900 ℃, the heat preservation time is 1-60 min, and the drawing speed is 0.1-1000 mu m/s, so that the FeAl column crystal is obtained.
Preferably, in the step (2), a water-cooled copper crucible suspension smelting furnace or a vacuum non-consumable arc smelting furnace is adopted to repeatedly smelt the raw materials for at least 4 times, and then the raw materials are cast by the vacuum non-consumable arc smelting furnace to obtain the FeAl alloy round rod with the diameter of 8-10 mm.
Preferably, in the step (3), the heating temperature is 1300-1600 ℃, the heat preservation time is 20-60 min, and the drawing speed is 5-500 μm/s.
Preferably, in the step (3), FeAl columnar crystals with the diameter of 8-10 mm and the length of 6-13 cm are obtained through directional solidification.
Compared with the prior art, the invention has the following remarkable advantages:
(1) the FeAl alloy prepared by the invention has a columnar crystal structure, eliminates a transverse crystal boundary, improves the comprehensive mechanical property of the alloy, and effectively solves the problems of poor plasticity and toughness, low strength and the like of the alloy.
(2) The method utilizes the unique characteristics of the Bridgman directional solidification device to prepare the FeAl alloy with the columnar crystal structure in one step, and has simple preparation method and lower process cost.
Drawings
FIG. 1 is a binary system phase diagram of FeAl alloy.
FIG. 2 is a scanning microstructure of a directionally solidified FeAl alloy sheet of example 1 (a is a scanning image, and b is a table of the midpoint scanning compositions in a).
FIG. 3 is a micrograph and optical micrograph of a directionally solidified FeAl alloy of example 1 (a is the as-cast region, b is the competing region, c is the stable region, and d is the magnified region in c).
FIG. 4 is a graph showing the quasi-static compression of example 1 with as-cast FeAl alloy.
FIG. 5 is a micrograph of a directionally solidified FeAl alloy of example 2.
FIG. 6 is a micrograph of a directionally solidified FeAl alloy of example 3.
FIG. 7 is a micrograph of a directionally solidified FeAl alloy of example 3.
FIG. 8 is a micrograph of a directionally solidified FeAl alloy of comparative example 1.
FIG. 9 is a micrograph of a directionally solidified FeAl alloy of comparative example 2.
FIG. 10 is a micrograph of a directionally solidified FeAl alloy of comparative example 3.
Detailed Description
The invention is described in detail below with reference to the figures and examples.
Example 1
(1) According to a binary system phase diagram of the FeAl alloy shown in figure 1, the proportioning component is Fe40Al60The alloy of (1).
(2) Repeatedly smelting the raw materials for at least 4 times by using a water-cooled copper crucible suspension smelting furnace, and then casting by using a vacuum non-consumable arc smelting furnace to obtain a FeAl alloy round rod with the diameter of 8 mm;
(3) under the protection of argon, a Bridgman directional solidification device is adopted to directionally solidify the cylindrical rod master alloy, the heating temperature is 1380 ℃, the heat preservation time is 20min, the drawing speed is 100 mu m/s, and finally the FeAl column crystal with the diameter of 8mm and the length of 6cm is obtained.
Point scanning is carried out on the selected area of the microscopic morphology, and the black structure is FeAl phase, and the white structure is FeAl phase2And (4) phase(s). As is clear from FIG. 1 and FIG. 2, around 1102 ℃ ε → FeAl + FeAl occurs2Phase change, epsilon phase generation of FeAl + FeAl2And (4) lamellar organization. The specific structure is shown in FIG. 3, and thus a FeAl alloy having a columnar crystal structure can be obtained. As can be seen from FIG. 4, the compression properties of the FeAl alloy having the columnar structure are higher than those of the FeAl alloy in the as-cast stateThe elongation is about 3 times higher and the elongation is about 1 time higher.
Example 2
Adopts the component Fe45Al55The other steps are the same as in example 1, except that: during directional solidification, the heating temperature is 1600 ℃, the holding time is 60min, and the drawing speed is 300 mu m/s, so that the FeAl alloy with the columnar crystal structure as shown in example 1 can still be obtained, and the micrograph thereof is shown in FIG. 5. The compression performance of the alloy is about 2 times higher than that of cast FeAl alloy, and the elongation is about 1 time higher.
Example 3
Adopts the component Fe37Al63The other steps are the same as in example 1, except that: during directional solidification, the heating temperature is 1500 ℃, the holding time is 40min, the drawing speed is 500 μm/s, and the FeAl alloy with the columnar crystal structure as described in example 1 can still be obtained, and the micrograph thereof is shown in FIG. 6. The compression performance of the alloy is about 2 times higher than that of cast FeAl alloy, and the elongation is about 1 time higher.
Example 4
Adopts the component Fe40Al60The other steps are the same as in example 1, except that: the holding time for directional solidification is 30min, the drawing rate is 5 μm/s, and the FeAl alloy with the columnar crystal structure as described in example 1 can still be obtained, and the micrograph thereof is shown in FIG. 7. The compression performance of the alloy is about 3 times higher than that of cast FeAl alloy, and the elongation is about 1 time higher.
Comparative example 1
Adopts the component Fe35Al65The other steps are the same as those of example 1, and a stable-section FeAl alloy without columnar crystal structure is obtained, and a micrograph thereof is shown in FIG. 8.
Comparative example 2
Adopts the component Fe47Al53The other steps are the same as those of example 1, and a stable-section FeAl alloy without columnar crystal structure is obtained, and a micrograph thereof is shown in FIG. 9.
Comparative example 3
Adopts the component Fe40Al60Under the growth rate of 1100 μm/s, and other conditionsIn the same manner as in example 1, a FeAl alloy having a stable-stage columnar-crystal-free structure was obtained, and its micrograph is shown in FIG. 10.
Claims (5)
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114433823A (en) * | 2022-01-19 | 2022-05-06 | 南京理工大学 | Oriented ZrCr-based alloy and preparation method thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0465686A1 (en) * | 1990-07-07 | 1992-01-15 | Asea Brown Boveri Ag | Oxidation- and corrosion resistant alloy for parts subjected to medium high temperatures and based on doped iron trialuminide Fe3Al |
| CN103789598A (en) * | 2014-02-28 | 2014-05-14 | 南京理工大学 | A kind of oriented TiAl-based alloy and its preparation method |
| CN105821470A (en) * | 2016-04-14 | 2016-08-03 | 南京理工大学 | Dual-structure titanium aluminum (TiAl) alloy and preparation method thereof |
| CN110090942A (en) * | 2019-06-06 | 2019-08-06 | 西安建筑科技大学 | The method that the multifunctional integrated material of Fe-Al-Ta is prepared using Bridgman directional solidification technique |
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- 2021-06-11 CN CN202110653471.2A patent/CN113528926A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0465686A1 (en) * | 1990-07-07 | 1992-01-15 | Asea Brown Boveri Ag | Oxidation- and corrosion resistant alloy for parts subjected to medium high temperatures and based on doped iron trialuminide Fe3Al |
| CN103789598A (en) * | 2014-02-28 | 2014-05-14 | 南京理工大学 | A kind of oriented TiAl-based alloy and its preparation method |
| CN105821470A (en) * | 2016-04-14 | 2016-08-03 | 南京理工大学 | Dual-structure titanium aluminum (TiAl) alloy and preparation method thereof |
| CN110090942A (en) * | 2019-06-06 | 2019-08-06 | 西安建筑科技大学 | The method that the multifunctional integrated material of Fe-Al-Ta is prepared using Bridgman directional solidification technique |
Non-Patent Citations (1)
| Title |
|---|
| A.SCHERF ET AL.: "Orientation relationship of eutectoid FeAl and FeAl2", 《JOURNAL OF APPLIED CRYSTALLOGRAPHY》 * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114433823A (en) * | 2022-01-19 | 2022-05-06 | 南京理工大学 | Oriented ZrCr-based alloy and preparation method thereof |
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