Alloy based on aluminum, the product of this alloy and method of manufacturing

 

The invention relates to the field of metallurgy, in particular to aluminum alloys of the aluminum-magnesium-silicon, including for the manufacture of solid semi-finished products obtained by pressing, rolling, punching, and can be used in industrial engineering, construction, and automotive industries. The proposed alloy, a product made therefrom, and method of manufacturing this product. The alloy contains components in the following ratio, wt.%: magnesium 0,25-1,5, silicon 0.3 to 1.5, the Titan of 0.005 to 0.15, iron 0,05-0,7, zinc of 0.001 to 1.0, at least one metal selected from the group comprising Nickel and cobalt of 0.001 to 0.18 at least one metal selected from the group including manganese 0,001-1,2, chrome 0,001-0,35, zirconium, about 0.001-0.25, scandium 0,001-0,40, aluminum else, the amount of Fe+(Ni and/or Co)0.6 ratio Fe/(Ni and/or Co)2, and the ratio of Fe/Mg2. B private embodiments of the invention, the alloy may contain at least one modifier, and/or at least one reinforcing metal and/or at least one metal, which improves the mechanical machinability. This method includes obtaining an ingot of an alloy based on aluminum, homogenization if the> is below the solidus of the alloy and the heating rate between the steps is not more than 30 deg/h, hot deformation in the temperature range with a lower limit of the temperature solvus phase of Mg2Si minus 200oWith,and the upper limit of the temperature solvus phase of Mg2Si plus 10oWith, and heat treatment including quenching and aging. The technical result of the invention is to improve the stability of the alloy to intergranular corrosion, the improvement of impact strength at room and low temperatures, improved weldability. 3 S. and 6 C.p. f-crystals, 2 tab.

The invention relates to the field of metallurgy, in particular to aluminum alloys of the aluminum-magnesium-silicon, including for the manufacture of solid semi-finished products obtained by pressing, rolling, punching, and can be used in industrial engineering, construction, and automotive industries. Alloy, in particular, can be made of the power structure, including welded, to work at room and low temperatures, and welding materials.

The alloys of the aluminum-magnesium-silicon due to its high ductility in hot condition received shirokage all, such domestic alloys as AD31, AD and AD, as well as their counterparts abroad.

In the patent US 4113472 discovered this alloy system containing the following components, wt.%: Magnesium - 0,9-1,5 Silicon - 0,4-0,8 Copper - 0,9-1,5 At least one element from the group of Manganese Is 0.05-0.4 Iron - 0,05-0,4 Chrome - 0,05-0,4 Titanium - 0.2 V To 0.2
Zirconia - 0.2
Cobalt - 0.4
Nickel - 3.5
Aluminum - Rest
when this %Cu<%Mg+%Si, %Si<0,58 %Mg+0,25(%Mn+%Fe). Accordingly, this patent disclosed a product made of this alloy and method of manufacturing products made of this alloy, including the casting of the ingot, its homogenizing annealing, hot deformation and aging.

The closest rafting to the invention is the alloy disclosed in the application Japan JP 4311545. Alloy and accordingly the product is made of Negeb contain the following components, wt%:
Magnesium - 0,3-1,6
Silicon - 0,15-1,6
Nickel - 0,2-6,0
Iron - 0,35-1,2
And at least one element from the group:
Copper - 0,05-1,0
Zinc - 0,05-1,0
Manganese is 0.05 to 1.0
Zirconia - 0,05-0,2
Chrome - 0,05-1,0
Vanadium - 0,01-0,3
Titanium - 0,001-0,1
Bor - 0,001-0,05
the ratio Fe/Ni=1/2-3/2.

The closest way of manufacturing products made of alloys of the aluminum-magnesium-silicon opaluwa system aluminum-magnesium-silicon, its homogenization, hot deformation, quenching and aging.

Shortcomings listed technical solutions are low values of impact strength at room and low temperatures, high sensitivity to intergranular corrosion, limited assortment due to the low stability of the solid solution, poor weldability (low ductility and toughness of welded joints), which reduces the service life of the products from this alloy, limits the range of manufactured products and increases the complexity of their manufacture.

The objective of the invention is to improve the stability of the alloy to intergranular corrosion, the improvement of impact strength at room and low temperatures, improved weldability. All this extends the range manufactured from alloy products, increases service life and reduces the labor involved in their manufacture.

The problem is solved in that the base alloy of aluminum containing magnesium, silicon, titanium, iron, and zinc, optionally, contains at least one metal selected from the group comprising Nickel and cobalt, and at least one metal selected from the group comprising manganese, chromium, CI-0,15
Iron - 0,05-0,7
Zinc is 0.001 to 1.0
At least one metal selected from the group including:
Nickel and cobalt - 0,001-0,18
At least one metal selected from the group including:
Manganese is 0.001 to 1.2
Chrome - 0,001-0,35
Zirconium is 0.001 to 0.25
Scandium is 0.001-0,40
Aluminum - Rest
the amount of Fe+(Ni and/or Co)0.6 ratio Fe/(Ni and/or Co)2, and the ratio of Fe/Mg2.

In private embodiments of the invention the task is solved in that the alloy may further contain at least one modifier selected from the group containing, wt.%:
Boron is 0.0001-0.06 to
Carbon - 0,00001-0,01
Vanadium - 0,001-0,20
Cerium - Not more than 0.15
Yttrium - Not more than 0.15
Hafnium is Not more than 0.18
Molybdenum is Not more than 0.18
Beryllium is Not more than 0.05
Strontium - Not more than 0.10
or optionally contain at least one active metal selected from the group consisting of, in wt.%:
Copper is 0.001 to 1.2
Silver is 0.001 to 0.6
To improve the mechanical workability of the alloy it is advisable to enter at least one metal selected from the group consisting of, in wt.%:
The lead - Not more than 1.2
Bismuth is Not more than 0.8
Tin is Not more than 0.8
Indium - Not more than 0.6
For is for drinking, preparing these products, in line c who receive the ingot of the above alloy based on aluminum, then spend its homogenization in two stages - the first stage at a temperature 480-525oFor 10-90 min, the second at a temperature of at 3-50oC below the solidus of the alloy and the heating rate between the steps is not more than 30 deg/h, hot deformation in the temperature range with a lower limit of the temperature solvus phase of Mg2Si minus 200oWith, and the upper limit of the temperature solvus phase of Mg2Si plus 10oWith, and heat treatment including quenching and aging.

In private embodiments of the method after hot deformation perform cold deformation with a total degree of from 10 to 90%.

Cold deformation, it is desirable to carry out by rolling.

After quenching can hold the cold edit with a degree of 0.2-6%.

The invention consists in the following.

The chemical composition of the alloy is selected so that its structure was characterized by fine discharge phase in Al-Mg-Fe-Ni(Co), having a globular shape instead of large lamellar particle phase in Al-Fe and Al-Fe-Ni(Co) present in the known alloy. For this reduced the Nickel content to 0.18% by weight, and takeaway phase in Al-Mg-Fe-Ni(Co) outputs of the solid solution magnesium, increasing the ratio of silicon to magnesium, which increases the stability of the solid solution by increasing the solubility of silicon and zinc in solid solution, and this reduces the high-temperature grain boundary dissolution of solid solution and increases the strength and plastic properties of the alloy and its resistance to intergranular corrosion.

Increased stability of the solid solution can be obtained from massive alloy semi-finished products, expanding the range of manufactured from alloy products.

In addition, the formation of fine globular phase in Al-Mg-Fe-Ni(Co) instead of phase in Al-Fe and Al-Fe-Ni(Co) has a modifying effect on the structure grinds the grain and enhances the alloy resistance to dynamic loads at room and low temperatures.

The presence of a titanium alloy, and such elements EnterCriticalSection as manganese, chromium, zirconium and scandium in the declared amount is dramatically reduced grain growth when heated, for example, for hardening or hot deformation and significantly increase the tensile strength and ductility of welded joints of base metal from the alloy.

In special cases it is possible to introduce additional elements, e.g. the stage and melting, which ultimately helps to improve the final structure of the alloy. Some modifiers can be particularly useful in the manufacture of the claimed alloy products subjected to welding, or welding materials. Elements such as cerium, yttrium, hafnium, molybdenum, beryllium and strontium allow you to get tight welded connection, almost Ravnopravie being welded metal and the heat affected zone, characterized by fine-grained structure.

In some cases it may be useful to gain extra in strength while maintaining superior viscosity at room and low temperatures and high corrosion resistance. In this case, it is expedient to introduce the copper and/or silver in the claimed amounts.

The elements lead, bismuth, tin and indium, as a rule, present in residual amounts in all alloys of aluminum. However, they may be entered in the alloy to improve the machinability of the alloy by cutting or other machining. The best result is obtained if their content does not exceed given in the formula values.

The content of impurities in the alloy should not exceed the following values, wt.%:
Calcium-https://img.russianpatents.com/chr/8226.gif">10-5
The fluorine - 0,05
Sulfur - 0,005
Potassium - 0,05
Gallium - 0,05
The modes of the method of production also are selected in such a way as to obtain the optimum size distribution as soluble and insoluble phases, as well as to provide fine-grained structure in the products we offer alloy.

All this leads to increased resistance of the alloy intergranular corrosion, higher values of impact strength at room and low temperatures, higher values of strength and ductility of welded joints and, consequently, increase the service life of products, expanding the range of manufactured products from alloy and cut the costs of their production.

Examples. Cast billets130 mm and a flat section h mm chemical composition shown in table. 1.

Example 1.

The ingot of alloy 1 homogenized by mode: 480oC for 60 min, heated at a rate of 8oC/h to a temperature of 560oWith that on the 30oC below the solidus temperature, kept for 4 hours Then spent the hot deformation by pressing at a temperature of 420oWith that 150oWith lower temperature solvus phase of Mg2Si.

C is sue.

Then there was the cold deformation with the degree of 1.8% and aging at a temperature of 180oWith over 8 hours

Example 2. Flat ingot alloy 2 homogenized by mode: 515oC - 30 min, heated at a rate of 25oC/h to a temperature of 570oWith that in 10oC below the solidus temperature, kept for 4 h, the hot deformation by rolling was carried out at a temperature of 540oWith that 2oWith higher temperature solvus phase of Mg2Si. Quenching plate thickness of 40 mm was performed in water with a temperature of 38oSince, then, were aged at 180oWith over 8 hours

Example 3. The plate obtained in example 2, rolled in the cold for a thickness of 10 mm with the degree of cold deformation 75%, the obtained sheet was tempered by cooling in water 90oAfter quenching was performed cold deformation with a degree of 0.8%, and then were aging at a temperature of 180oWith over 8 hours

Data testing the mechanical and corrosion properties are given in table. 2.

As can be seen from the table. 2, the proposed alloy in comparison with the known is 5-10% higher values of strength of the base material, 20-40% higher values of the strength of the welded joint and 1.5-2 times greater ductility of the weld. He also ototype, not sensitive to intergranular corrosion.

Thus, the invention improves the stability of the alloy to intergranular corrosion, to improve impact strength at room and low temperatures, enhance strength and ductility of welded joints and base metal and, consequently, to increase the service life of products, to expand their range, and reduce the labor involved in their manufacture.


Claims

1. The base alloy of aluminum containing magnesium, silicon, titanium, iron, and zinc, characterized in that it additionally contains at least one metal selected from the group comprising Nickel and cobalt, and at least one metal selected from the group comprising manganese, chromium, zirconium and scandium in the following ratio, wt.%:

Magnesium 0,25 - 1,5

Silicon 0,3 - 1,5

Titanium is 0.005 to 0.15

Iron 0,05 - 0,7

Zinc 0,001 - 1,0

At least one metal,

selected from the group including

Nickel and cobalt 0,001 - 0,18

At least one metal,

selected from the group including

Manganese 0,001 - 1,2

Chrome 0,001 - 0,35

Zirconium 0,001 - 0,25

Scandium 0,001 - 0,40

Aluminum Else

the amount of Fe+(Ni and/or if">2.

2. Alloy under item 1, characterized in that it additionally contains at least one modifier selected from the group containing, wt.%:

Bor 0,0001 - 0,06

Carbon 0,00001 - 0,01

Vanadium 0,001 - 0,20

Cerium0,15

Yttrium0,15

Hafnium0,18

Molybdenum0,18

Beryllium0,05

Strontium0,10

3. Alloy under item 1 or 2, characterized in that it further comprises at least one reinforcing metal selected from the group consisting of, in wt.%:

Copper 0,001 - 1,2

The silver of 0.001 to 0.6

4. The alloy according to any one of paragraphs.1-3, characterized in that it additionally contains at least one metal selected from the group consisting of, in wt.%:

Lead1,2

Bismuth0,8

Tin0,8

Indies0,6

5. The product from an alloy based on aluminum, characterized in that it is made from an alloy according to any one of paragraphs.1-4 formulas.

6. A method of manufacturing a product from an alloy based on aluminum, including the production of an ingot of an alloy based on aluminum, its homogenization, hot deformation, suculenta in accordance with any of paragraphs.1-4, homogenization of the ingot in two stages: the first stage when 480-525For 10-90 min, the second at a temperature of at 3-50C below the solidus of the alloy and the heating rate between the steps is not more than 30 deg/h, hot deformation is carried out in a temperature range with a lower limit of the temperature solvus phase of Mg2Si minus 200C and an upper limit equal to the temperature solvus phase of Mg2Si plus 10With and conduct heat treatment including quenching and aging.

7. The method according to p. 6, characterized in that after hot deformation perform cold deformation with a total degree of from 10 to 90%.

8. The method according to p. 7, characterized in that the cold deformation is carried out by rolling.

9. The method according to any of paragraphs.6-8, characterized in that after quenching spend cool edit with a degree of 0.2-6%.

 

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