CN105483452A - High-strength alloy and preparation method thereof - Google Patents
High-strength alloy and preparation method thereof Download PDFInfo
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- CN105483452A CN105483452A CN201510912186.2A CN201510912186A CN105483452A CN 105483452 A CN105483452 A CN 105483452A CN 201510912186 A CN201510912186 A CN 201510912186A CN 105483452 A CN105483452 A CN 105483452A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
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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
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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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
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
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Abstract
The invention discloses high-strength alloy which is prepared from the following components in percentage by mass: 3.5-4.25 percent of iron, 8.2-10.39 percent of nickel, 2.5-3.7 percent of manganese, 1.12-1.38 percent of boron, 0.2-0.33 percent of tellurium, 2.5-3.8 percent of tungsten, 0.44-0.62 percent of platinum, 0.18-0.25 percent of scandium, 0.12-0.22 percent of holmium, 0.13-0.19 percent of rhenium and the rest of aluminum. The alloy is prepared by vacuum melting, refining, pressure casting, heat treatment and aging. Due to the reasonable preparation of components and contents, the aluminum alloy has enough mechanical property, particularly the mechanical property suitable for heavy load and high temperature usage environments; meanwhile, the process parameters of pressure casting and the pressure parameters of inert gases during refining are optimally selected, and the mechanical property of the alloy is improved.
Description
Technical field
The present invention relates to one one kinds of high-strength alloys and preparation method thereof, belong to alloy and manufacture field.
Background technology
Die casting is a kind of part of pressure die casting, use the pressure die casting machinery pressure die-casting machine installing casting die, metals such as being heated to be liquid copper, zinc, aluminium or zinc alloy is poured into the feeding mouth of pressure die-casting machine, through pressure die-casting machine die casting, cast out the copper of the shape and size of mould restriction, zinc, aluminium part or zinc alloy part, such part is just called die casting usually.Die casting has different calls in different places, as diecast parts, die-casting, die casting, die casting aluminium, die case zinc part, die casting copper piece, copper die casting, zine pressure casting, aluminium diecasting aluminium diecasting, aluminium pressure alloy-steel casting, zinc alloy diecasting part etc.Because metallic copper, zinc, aluminium and zinc alloy have good mobility and plasticity-, and casting processing is cast in the pressure die-casting machine having pressure, therefore aluminium diecasting can make various more complicated shape, also higher precision and smooth finish can be made, thus decrease the machining amount of foundry goods and the casting surplus of metallic copper, zinc, aluminium or zinc alloy significantly, not only save electric power, metallic substance, also greatly save labour cost; And copper, zinc, aluminium and zinc alloy have excellent thermal conductivity, less proportion and high workability; Thus die casting is widely used in the industry-by-industries such as automobile making, oil engine production, motorcycle manufacture, electric motor manufacture, oil pump manufacture, gearing manufacture, precision instrument, landscaping, power construction, building decoration.
In existing die casting use, the content of each element is different, and therefore spatial distribution differences is comparatively large in the alloy for each element, causes each alloy over-all properties different, particularly mechanical property differs greatly.
Summary of the invention
For overcoming above-mentioned deficiency, the object of the invention provides a kind of high-strength alloy and preparation method thereof, and this alloy is aluminium alloy, and hardness is high, wear resistance good.
The solution of the present invention is as follows: a kind of high-strength alloy, is grouped into by the following one-tenth according to mass percent:
Iron 3.5-4.25%, nickel 8.2-10.39%, manganese, 2.5-3.7%, boron 1.12-1.38%, tellurium 0.2-0.33%, tungsten 2.5-3.8%, platinum 0.44-0.62%, scandium 0.18-0.25%, holmium 0.12-0.22%, rhenium 0.13-0.19%, surplus is aluminium.
Further, be grouped into by the following one-tenth according to mass percent:
Iron 3.75-4.05%, nickel 8.85-9.69%, manganese, 2.68-3.55%, boron 1.25-1.31%, tellurium 0.25-0.32%, tungsten 3.1-3.56%, platinum 0.48-0.59%, scandium 0.18-0.22%, holmium 0.12-0.18%, rhenium 0.15-0.17%, surplus is aluminium.
Further, be grouped into by the following one-tenth according to mass percent: iron 3.86%, nickel 9.12%, manganese, 3.03%, boron 1.27%, tellurium 0.285%, tungsten 3.25%, platinum 0.51%, scandium 0.19%, holmium 0.156%, rhenium 0.16%, surplus is aluminium.
A preparation method for high-strength alloy, is characterized in that, comprises the following steps:
1) iron, nickel, manganese, boron, tellurium, tungsten, platinum, aluminium are put into vacuum melting furnace crucible, be evacuated to 8 × 10
-2more than Pa, starts to heat up, and after temperature rises to 842-935 DEG C, stops vacuumizing and be filled with rare gas element to 4 × 10 in vacuum melting furnace
4pa; Then continue to be warming up to 1220-1290 DEG C, aluminium alloy to be formed, is filled with rare gas element and stirs 30-40 minute in aluminium alloy, is cooled by aluminium alloy, obtains master alloy;
2) master alloy and scandium, holmium, rhenium are joined in vacuum melting furnace crucible, be evacuated to 8 × 10
-2more than Pa, starts to heat up, and after temperature rises to 842-935 DEG C, stops vacuumizing and be filled with rare gas element to 4 × 10 in vacuum melting furnace
4pa; Then continue to be warming up to 1220-1290 DEG C, treat that alloy dissolves completely, after refining leaves standstill 25-35 minute, after inspection bath composition is qualified, namely obtain refining liquid;
3) after refining liquid being cooled to 650-700 DEG C, die casting is preheated in the mold cavity of 250-275 DEG C to passing through, the refining liquid melt flow of wherein filling when type starts is 0.32m/s, casting pressure is 78MPa, fill type rate more than 63% after, the melt flow improving refining liquid is 106MPa to 2.25m/s, casting pressure, terminates until fill type die casting;
4) thermal treatment: by die casting foundry goods under 425 DEG C of conditions after homogenizing 28-32h after shrend to room temperature, then be warming up to the ageing treatment that 165-175 DEG C is carried out 12-15h, obtain alloy.
The present invention is by great many of experiments, and scandium, holmium and rhenium in adding in the basic components of research, can ensure that alloy has enough mechanical properties, particularly be applicable to the mechanical property under heavy duty, applied at elevated temperature environment.When the processing parameter of simultaneously optimum option die casting and refining, inert gas pressure parameter, improves its alloy mechanical property.The present invention not only has excellent ambient temperature mechanical properties, even if still can meet service requirements under the condition more than 150 DEG C, is particularly useful for making the die casting under high temperature heavy load working conditions.
Embodiment
Below in conjunction with embodiment, the present invention will be further described.
Embodiment 1
A kind of high-strength alloy, is grouped into by the following one-tenth according to mass percent: iron 3.86%, nickel 9.12%, manganese, 3.03%, boron 1.27%, tellurium 0.285%, tungsten 3.25%, platinum 0.51%, scandium 0.19%, holmium 0.156%, rhenium 0.16%, surplus is aluminium.
Preparation method, comprises the following steps:
1) iron, nickel, manganese, boron, tellurium, tungsten, platinum, aluminium are put into vacuum melting furnace crucible, be evacuated to 8 × 10
-2more than Pa, starts to heat up, and after temperature rises to 915 DEG C, stops vacuumizing and be filled with rare gas element to 4 × 10 in vacuum melting furnace
4pa; Then continue to be warming up to 1285 DEG C, aluminium alloy to be formed, in aluminium alloy, be filled with rare gas element and stir 36 minutes, aluminium alloy is cooled, obtains master alloy;
2) master alloy and scandium, holmium, rhenium are joined in vacuum melting furnace crucible, be evacuated to 8 × 10
-2more than Pa, starts to heat up, and after temperature rises to 915 DEG C, stops vacuumizing and be filled with rare gas element to 4 × 10 in vacuum melting furnace
4pa; Then continue to be warming up to 1285 DEG C, treat that alloy dissolves completely, refining left standstill after 36 minutes, namely obtained refining liquid after inspection bath composition is qualified;
3) after refining liquid being cooled to 700 DEG C, die casting is preheated in the mold cavity of 270 DEG C to passing through, the refining liquid melt flow of wherein filling when type starts is 0.32m/s, casting pressure is 78MPa, fill type rate more than 63% after, the melt flow improving refining liquid is 106MPa to 2.25m/s, casting pressure, terminates until fill type die casting;
4) thermal treatment: by die casting foundry goods under 425 DEG C of conditions after homogenizing 29h after shrend to room temperature, then be warming up to the ageing treatment that 170 DEG C are carried out 12-15h, obtain alloy.
Embodiment 2
A kind of high-strength alloy, be grouped into by the following one-tenth according to mass percent: iron 3.8%, nickel 9.1%, manganese 3.11%, boron 1.28%, tellurium 0.25-0.32%, tungsten 3.35%, platinum 0.52%, scandium 0.19%, holmium 0.15%, rhenium 0.16%, surplus is aluminium.
Preparation method is with embodiment 1.
Embodiment 3
A kind of high-strength alloy, is grouped into by the following one-tenth according to mass percent: iron 3.79%, nickel 9.1%, manganese, 2.99%, boron 1.28%, tellurium 0.31%, tungsten 3.36%, platinum 0.58%, scandium 0.19%, holmium 0.14%, rhenium 0.15%, surplus is aluminium.
Preparation method is with embodiment 1.
Embodiment 4
A kind of high-strength alloy, is grouped into by the following one-tenth according to mass percent:
Iron 4.1%, nickel 8.89%, manganese 3.6%, boron 1.19%, tellurium 0.2-0.33%, tungsten 2.9%, platinum 0.48%, scandium 0.21%, holmium 0.18%, rhenium 0.14%, surplus is aluminium.
Preparation method is with embodiment 1.
Embodiment 5
A kind of high-strength alloy, is grouped into by the following one-tenth according to mass percent:
Iron 3.6%, nickel 8.85%, manganese, 2.84%, boron 1.25%, tellurium 0.28%, tungsten 2.89%, platinum 0.51%, scandium 0.214%, holmium 0.175%, rhenium 0.154%, surplus is aluminium.
Preparation method is with embodiment 1.
Comparative example 1
Not containing scandium, all the other compositions and content consistent with embodiment 1.
Comparative example 2
Not containing holmium, all the other compositions and content consistent with embodiment 1.
Comparative example 3
Not rhenium-containing, all the other compositions and content consistent with embodiment 1.
Comparative example 4
Not containing scandium, holmium, rhenium, all the other compositions and content consistent with embodiment 1.
The intensity of obtained alloy system and the result of hardness as shown in table 1.
Table 1
| Group | σ B room temperature（MPa） | Hardness Room temperature（HB） | σ b150℃（Mpa） | Hardness Room temperature（HB） |
| Embodiment 1 | 518 | 227 | 458 | 187 |
| Embodiment 2 | 508 | 215 | 432 | 172 |
| Embodiment 3 | 509 | 212 | 438 | 165 |
| Embodiment 4 | 502 | 208 | 422 | 178 |
| Embodiment 5 | 498 | 203 | 418 | 161 |
| Comparative example 1 | 415 | 145 | 345 | 128 |
| Comparative example 2 | 423 | 125 | 332 | 115 |
| Comparative example 3 | 428 | 143 | 309 | 102 |
| To routine 4 | 416 | 135 | 312 | 113 |
As shown in Table 1, scandium, holmium, rhenium have important impact for the intensity of alloy system and hardness, not containing scandium, holmium, these three kinds of compositions of rhenium, cause the destruction of alloy system whole machine balancing and affect the usefulness of other alloying elements, causing the obvious deficiency of hot strength.The interpolation of scandium, holmium, rhenium lacks wherein a kind of composition, and the room temperature strength of alloy system can be caused all can not to meet the requirement of use.Scandium, holmium, rhenium have played stable alloy system tissue, avoid the deterioration of the zinc alloy system mechanical property caused due to thermal treatment, timeliness and heavy duty, applied at elevated temperature environment, can find out that the two collaboratively can play maximum stabilization.
The present invention has excellent mechanical property, enough under heavy duty, applied at elevated temperature environment, still keeps enough physical strengths and hardness.
Comparative example 5-8, the chemical composition of alloy is identical with embodiment 1, the optimization selection of the processing parameter in paper examines press casting procedure, parameter choose and results of property see table 2.
Although adopt low speed, at a high speed two kinds of different melt flow to be techniques well known in the art to control the defects such as pore in press casting procedure, as shown in Table 2, melt flow and casting pressure how is selected still to have a great impact.
For melt flow and the casting pressure of low-speed stage of the present invention, melt flow should be controlled at 0.32/s, lower melt flow can cause melt cooling too fast and affect the die casting performance of melt, thus the final mechanical property worsening alloy, and be also unfavorable for the raising of production efficiency.Higher melt flow then can cause the appearance of turbulent flow and easily be involved in gas and oxide inclusion, can cause the rapid solidification of local melt simultaneously and produce the defects such as pore.The increase of casting pressure obviously can improve the mechanical property of material, mainly the raising of alloy compactness that produces of pressure increase and the minimizing of defect, and in order to ensure this effect, casting pressure of the present invention is 78Pa.
For melt flow and the casting pressure of high speed stage, should control melt flow is 2.25s, and casting pressure is 106Pa, and it, for press casting procedure and the impact of alloy mechanical property and the similar of low-speed stage, repeats no more.The present invention has the die-casting technological parameter being most suitable for it, against the decline that all may cause alloy property in the most optimized parameter.
Table 2
| Group | Melt flow V1(m/s) | Casting pressure F1(MPa) | Melt flow V2(m/s) | Casting pressure F2(MPa) | σ B room temperature（MPa） | Hardness Room temperature（HB） |
| Embodiment 1 | 0.32 | 78 | 2.25 | 106 | 528 | 228 |
| Comparative example 5 | 0.3 | 70 | 2.0 | 100 | 415 | 128 |
| Comparative example 6 | 0.38 | 80 | 3.0 | 110 | 438 | 133 |
| Comparative example 7 | 0.35 | 74 | 2.5 | 100 | 428 | 122 |
| Comparative example 8 | 0.29 | 75 | 2.4 | 109 | 438 | 129 |
Comparative example 9-10, the chemical composition of alloy is identical with embodiment 1, the optimization selection of inert gas pressure during paper examines refining, parameter choose and results of property see table 3.
Table 3
| Group | Inert gas pressure (× 104Pa) | σ B room temperature（MPa） | Hardness Room temperature（HB） |
| Embodiment 1 | 4 | 525 | 218 |
| Comparative example 9 | 3 | 425 | 152 |
| Comparative example 10 | 5 | 510 | 198 |
As shown in Table 3, inert gas pressure can not be too low, can not play a role and obtain stable mechanical property, and too high inert gas pressure then can affect the hardness of alloy.
To those skilled in the art, obviously the invention is not restricted to the details of above-mentioned one exemplary embodiment, and when not deviating from spirit of the present invention or essential characteristic, the present invention can be realized in other specific forms.Therefore, no matter from which point, all should embodiment be regarded as exemplary, and be nonrestrictive, scope of the present invention is limited by claims instead of above-mentioned explanation, and all changes be therefore intended in the implication of the equivalency by dropping on claim and scope are included in the present invention.
In addition, be to be understood that, although this specification sheets is described according to embodiment, but not each embodiment only comprises an independently technical scheme, this narrating mode of specification sheets is only for clarity sake, those skilled in the art should by specification sheets integrally, and the technical scheme in each embodiment also through appropriately combined, can form other embodiments that it will be appreciated by those skilled in the art that.Although give detailed description and explanation to the specific embodiment of the present invention above; but what should indicate is; we can carry out various equivalence according to conception of the present invention to above-mentioned embodiment and change and amendment; its function produced do not exceed that specification sheets contains yet spiritual time, all should within protection scope of the present invention.
Claims (4)
1. a high-strength alloy, is characterized in that, is grouped into by the following one-tenth according to mass percent:
Iron 3.5-4.25%, nickel 8.2-10.39%, manganese, 2.5-3.7%, boron 1.12-1.38%, tellurium 0.2-0.33%, tungsten 2.5-3.8%, platinum 0.44-0.62%, scandium 0.18-0.25%, holmium 0.12-0.22%, rhenium 0.13-0.19%, surplus is aluminium.
2. high-strength alloy according to claim 1, is characterized in that, is grouped into by the following one-tenth according to mass percent:
Iron 3.75-4.05%, nickel 8.85-9.69%, manganese, 2.68-3.55%, boron 1.25-1.31%, tellurium 0.25-0.32%, tungsten 3.1-3.56%, platinum 0.48-0.59%, scandium 0.18-0.22%, holmium 0.12-0.18%, rhenium 0.15-0.17%, surplus is aluminium.
3. the high-strength alloy of die casting according to claim 1, it is characterized in that, be grouped into by the following one-tenth according to mass percent: iron 3.86%, nickel 9.12%, manganese, 3.03%, boron 1.27%, tellurium 0.285%, tungsten 3.25%, platinum 0.51%, scandium 0.19%, holmium 0.156%, rhenium 0.16%, surplus is aluminium.
4. the preparation method of the high-strength alloy according to claim arbitrary in claim 1-3, is characterized in that, comprise the following steps:
1) iron, nickel, manganese, boron, tellurium, tungsten, platinum, aluminium are put into vacuum melting furnace crucible, be evacuated to 8 × 10
-2more than Pa, starts to heat up, and after temperature rises to 842-935 DEG C, stops vacuumizing and be filled with rare gas element to 4 × 10 in vacuum melting furnace
4pa; Then continue to be warming up to 1220-1290 DEG C, aluminium alloy to be formed, is filled with rare gas element and stirs 30-40 minute in aluminium alloy, is cooled by aluminium alloy, obtains master alloy;
2) master alloy and scandium, holmium, rhenium are joined in vacuum melting furnace crucible, be evacuated to 8 × 10
-2more than Pa, starts to heat up, and after temperature rises to 842-935 DEG C, stops vacuumizing and be filled with rare gas element to 4 × 10 in vacuum melting furnace
4pa; Then continue to be warming up to 1220-1290 DEG C, treat that alloy dissolves completely, after refining leaves standstill 25-35 minute, after inspection bath composition is qualified, namely obtain refining liquid;
3) after refining liquid being cooled to 650-700 DEG C, die casting is preheated in the mold cavity of 250-275 DEG C to passing through, the refining liquid melt flow of wherein filling when type starts is 0.32m/s, casting pressure is 78MPa, fill type rate more than 63% after, the melt flow improving refining liquid is 106MPa to 2.25m/s, casting pressure, terminates until fill type die casting;
4) thermal treatment: by die casting foundry goods under 425 DEG C of conditions after homogenizing 28-32h after shrend to room temperature, then be warming up to the ageing treatment that 165-175 DEG C is carried out 12-15h, obtain alloy.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106756267A (en) * | 2016-12-05 | 2017-05-31 | 郑州丽福爱生物技术有限公司 | A kind of wear-resistant aluminium alloy material and preparation method thereof |
| WO2017124832A1 (en) * | 2016-01-18 | 2017-07-27 | 苏州大学张家港工业技术研究院 | Method for forming laser rapidly-formed part |
| CN107654774A (en) * | 2016-07-26 | 2018-02-02 | 住友理工株式会社 | Plastic working aluminium die casting product manufacture method and the fixture construction using the die casting product |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB595929A (en) * | 1945-07-10 | 1947-12-23 | Rupert Martin Bradbury | An improved aluminium base alloy |
| EP2105518A2 (en) * | 2008-03-25 | 2009-09-30 | Daido Metal Company Ltd. | Sliding bearing |
| CN103849797A (en) * | 2014-01-16 | 2014-06-11 | 滁州东润电子科技有限公司 | Casting aluminum alloy material for light-emitting diode (LED) lamp radiator and preparation technology thereof |
-
2015
- 2015-12-11 CN CN201510912186.2A patent/CN105483452A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB595929A (en) * | 1945-07-10 | 1947-12-23 | Rupert Martin Bradbury | An improved aluminium base alloy |
| EP2105518A2 (en) * | 2008-03-25 | 2009-09-30 | Daido Metal Company Ltd. | Sliding bearing |
| CN103849797A (en) * | 2014-01-16 | 2014-06-11 | 滁州东润电子科技有限公司 | Casting aluminum alloy material for light-emitting diode (LED) lamp radiator and preparation technology thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2017124832A1 (en) * | 2016-01-18 | 2017-07-27 | 苏州大学张家港工业技术研究院 | Method for forming laser rapidly-formed part |
| CN107654774A (en) * | 2016-07-26 | 2018-02-02 | 住友理工株式会社 | Plastic working aluminium die casting product manufacture method and the fixture construction using the die casting product |
| CN106756267A (en) * | 2016-12-05 | 2017-05-31 | 郑州丽福爱生物技术有限公司 | A kind of wear-resistant aluminium alloy material and preparation method thereof |
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Application publication date: 20160413 |