RU2833648C1 - Wear-resistant antifriction aluminium-based composite material and method for its production - Google Patents

Abstract

FIELD: metallurgy.

SUBSTANCE: invention relates to metallurgy of aluminium-based alloys used in sliding friction assemblies. Wear-resistant antifriction aluminium-based composite material contains the following, wt.%: tin from 37 to less than 37.7 or from more than 37.7 to 38; Al₃Fe 17-36; aluminium – the rest. Method of producing a wear-resistant aluminium-based antifriction composite material includes preparing a mixture of powders of aluminium, tin and iron, moulding a compact, its sintering and subsequent compaction, wherein the compact is sintered at temperature of 710-720 °C with holding at said temperature, and compaction is carried out in a closed die at temperature of 250-260 °C and pressure of 305-350 MPa, wherein material of said composition is obtained. Material is characterized by high strength and wear resistance.

EFFECT: improved tribotechnical properties.

3 cl, 4 dwg, 2 tbl, 4 ex

Description

The invention relates to the field of powder metallurgy of aluminum-based alloys used in sliding friction units.

An aluminum-based antifriction alloy is known from Russian patent 2643284, C22C 21/10, C22C 21/06, published 31.01.2018 [1], which can be used to manufacture parts operating under sliding friction conditions. The aluminum-based antifriction alloy contains, wt.%: silicon <1.2; copper 0.7-1.1; magnesium 3.5-5.5; zinc 4.0-5.5; tin 3.5-4.5; manganese <1.0; titanium 0.05-0.25; silicon <1.2; iron <1.2; aluminum is the rest. According to the second embodiment, the aluminum-based alloy contains, wt. %: silicon <1.2, copper 0.7-1.1, magnesium 3.5-5.5, zinc 4.0-5.5, tin 3.5-4.5, manganese <1.0, zirconium 0.05-0.25, silicon <1.2, iron <1.2, aluminum - the rest. In both variants, each of the other impurities individually contains no more than 0.2%, and the sum of all impurities should not exceed 1.2%. The technical result of the invention is to reduce metal consumption, increase the reliability and stability of the parts.

An antifriction aluminum casting alloy for monometallic plain bearings is known from the Russian Federation patent 2702531, C22C 21/16, C22C 21/18, published 08.10.2019 [2]. The antifriction aluminum casting alloy for monometallic plain bearings contains, by weight %: tin 4.5-8, lead 2-4, copper 3.5-4.5, silicon 0.6-1.0, zinc 2.0-3.0, magnesium 1.5-2.5, titanium 0.03-0.2, chromium 0.8-1.2, aluminum - the rest. The alloy is characterized by high values of scuffing load, running-in area, tensile strength, relative elongation and hardness of the alloy with a decrease in the average specific load.

The main disadvantage of the above technical solutions is the large number of alloying additives, which significantly increases the cost of products made from antifriction aluminum alloys, the low content of the soft tin phase, which does not ensure reliable operation of the friction unit, and the low wear resistance of the alloys under dry friction.

A method for producing a wear-resistant antifriction alloy is known from Russian patent 2552208, C22F 1/04, C22C 1/04, C22C 21/00, B22F 3/24, published 10.06.2015 [3]. The method for producing an antifriction wear-resistant alloy based on aluminum includes mixing 35-45% by weight of elemental tin powders and aluminum powders - the rest, forming briquettes with a porosity of 12-18%, sintering them in a non-oxidizing atmosphere at a temperature of 585-615 ° C for 45-60 minutes, followed by angular pressing of the sintered alloy while maintaining the orientation of the material flow plane during plastic processing at a deformation intensity of at least 100%. The technical result of the invention is to ensure maximum wear resistance of the alloy under dry friction.

A wear-resistant aluminum-based composite material and a method for producing it are known from Russian patent 2714005, C22C 21/02, B22F 3/16, B22F 3/24, 11.02.2020 [4]. The wear-resistant aluminum-based composite material contains silicon and tin, while it contains aluminum in the form of a matrix alloyed with 12% silicon, and the mass content of tin in the composite is 10-40% relative to the weight of the matrix. The method for producing an aluminum-based composite material includes preparing a mixture of initial powders, forming a compact, sintering, and then compacting it. In this case, the molding of the pressing is carried out to a porosity of 10-15%, sintering is carried out using 2-stage heating, first at a temperature of 550±10°C, then the temperature is increased to 570±5°C and maintained at the specified temperature, after which the sintered pressing is compacted to a porosity of less than 1% in a closed die at a temperature above the melting point of tin. The invention is aimed at obtaining a composite material based on aluminum, which has improved tribotechnical properties, in particular, increased strength and wear resistance.

The main disadvantage of the last two technical solutions mentioned above is the low load-bearing capacity and wear resistance under dry friction of the obtained alloys.

A wear-resistant antifriction material based on a two-phase Al-Sn alloy doped with iron and a method for producing it described in patent RU 2789324, C22C 21/00, published 01.02.2023 [5] were selected as a prototype. The wear-resistant antifriction composite material based on aluminum contains, by weight %: tin 30-49, iron 5.5-13.4, aluminum the rest, while after sintering, particles of solid iron aluminides are formed in the material. The method for producing a composite material based on aluminum includes preparing a powder mixture from powder components, forming a pressing, two-stage sintering followed by its compaction. The pressing is formed to a porosity of 8-12%, sintered first at a temperature of 525-535°C, then the sintering temperature is increased to 570-710°C and maintained at the specified temperature, after which the sintered pressing is compacted under a pressure of 295-305 MPa in a closed die. The material is characterized by high mechanical and tribotechnical properties.

The main disadvantage of the prototype is the presence of a two-stage sintering mode of powder compacts, the first stage of which is due to the need for uniform distribution of liquid tin over the compact and completion of the reaction between Al and Fe with the formation of iron aluminides Al ₃ Fe before the subsequent increase in the sintering temperature. Otherwise, the solid particles of the new phase are insufficient to form a framework that supports the shape of the sintered compact in the presence of a melt.

Another disadvantage caused by in-situ alloy formation of aluminides is the uneven distribution of Al ₃ Fe particles throughout the volume of the sample in the form of agglomerates of small particles formed in place of the original iron powders, which negatively affects the mechanical and tribological properties of the sintered composite.

The technical problem that the proposed invention is aimed at solving is the development of a wear-resistant antifriction composite material based on aluminum and a method for producing it.

The technical result of the invention is the production, using the claimed method, of a composite material of the claimed composition with a uniform distribution of solid phase particles throughout the volume of the material, possessing improved tribotechnical properties, in particular increased strength and wear resistance.

The specified technical result is achieved in that the wear-resistant antifriction composite material based on aluminum contains tin and iron aluminide, and it contains components in the following ratio, wt.%: tin from 37 to less than 37.7 or from more than 37.7 to 38, Al ₃ Fe 17-36, aluminum - the rest.

The specified technical result is also achieved by the fact that the method for producing a composite material based on aluminum includes preparing a mixture of aluminum, tin and iron powders, forming a compact, sintering it and then compacting it, wherein the compact is sintered at a temperature of 710-720°C with holding at the specified temperature, and compaction is carried out in a closed die at a temperature of 250-260°C and a pressure of 305-350 MPa, whereby a material is obtained containing components in the following ratio, wt. %: tin from 37 to less than 37.7 or from more than 37.7 to 38, Al ₃ Fe 17-36, aluminum - the rest. Formation of the compact is carried out up to 8-12%.

Disclosure of the essence of the invention.

The proposed aluminum-based material contains tin, the volume fraction of which is maintained constant at 20%, and part of the aluminum in the matrix is replaced by the Al ₃ Fe compound introduced into the sintered mixture in the form of fine powders. The composition of the alloys under study is given in Table 1.

Table 1. Elemental composition (% mass/% vol) and theoretical density of sintered alloys of the Al-Fe-Sn system.

Element/Density of Alloy Alloy number and its composition
(% w/% vol) 1 2 3 4 5 Sn/ 39/20 38/20 38/20 37/20 37/20 _Al3Fe / 14/13 17/18 24/24 30/31 36/38 Al/ Ost. Ost. Ost. Ost. Ost. /ρ _t , g/cm ³ 3.76 3.8 3.89 3.96 4.05

The main cause of adhesive wear of aluminum alloys is their tendency to seize with a steel counterbody during boundary or dry friction. In order to reduce its intensity, tin and/or another insoluble low-melting metal are introduced into aluminum, which can be squeezed out onto the friction surface and spread into a thin layer, preventing the surfaces of the aluminum bearing and shaft from seizing. With an increase in the concentration of these metals, the seizing pressure increases, and the intensity of adhesive wear decreases. However, despite the positive anti-seize effect of these metals, their content in aluminum is limited. For example, GOST 14113-78 allows the use of Al-Sn alloys with a tin concentration of no more than 20% (~10% vol.) as bearing materials in the presence of liquid lubrication and a pressure of up to 30 MPa.

The limitations on tin concentration are due to the fact that during melt crystallization it is pushed to the periphery of growing aluminum grains and forms a network of thin soft layers that reduce the bearing capacity of the matrix. At the same time, it is not possible to achieve the division of the tin grid into isolated inclusions even at very high melt cooling rates. For this reason, GOST recommends using two-component alloys with a high tin content in the form of thin coatings on durable bearing liners - multilayer expensive and difficult to manufacture parts.

To manufacture monometallic bearings from Al-Sn-based alloys, various elements that strengthen the aluminum matrix are additionally introduced into their composition - copper, zinc, magnesium, as well as silicon and transition metals that form solid intermetallic particles when interacting with aluminum. However, if the matrix frame is weakened by a large number of intergranular tin layers, then the indicated measures aimed at improving wear resistance and increasing the load-bearing capacity of the material due to strengthening the matrix grains are ineffective.

The authors found that if the Al-Sn alloys are obtained not by casting, but by sintering a mixture of elemental powders, then the presence of Al grains with an average number of cohesive boundaries between the nearest neighbors of less than 2 becomes predominant only at a volume fraction of tin above 20% (>40% by weight). That is, at the specified concentration of tin and less than Al, the framework is preserved, as is its ability to withstand external load.

After sintering, the aluminum matrix grain material is in a well-annealed state, has a low yield point σ _0.2 = 50-60 MPa and low hardness. When loading such material, the matrix begins to deform already at a low load, which is accompanied by an undesirable change in the shape and size of the product. That is, the value of σ _0.2 is important for an antifriction material, since it determines the permissible load on friction bearings made from it. During deformation, the grains are strengthened, the value of σ _0.2 increases, and the matrix stops flowing under the current load.

The same effect can be achieved if the sintered material is subjected to intensive strengthening treatment by rolling or extrusion. However, in this case the transverse dimensions of the samples are greatly reduced, and the range of possible products from them is accordingly narrowed. Another undesirable effect of intensive deformation is the thinning of the tin layers sandwiched between the grains and a decrease in their plasticity resource, which leads to low plasticity of the entire material [3]. Thin layers begin to collapse, forming delaminations along the boundaries of the matrix grains.

In order to avoid the use of strengthening intensive deformation treatment and the resulting decrease in the plasticity of the sintered material, the authors proposed adding powders of hard refractory particles to the sintered mixture of Al and Sn powders so that they, located between the matrix grains, prevent their convergence and thinning of the intergranular tin layers. Since the hard particles in this case are in contact with both the Al grains and the tin surrounding them, it is desirable for them to be well wetted by both tin and aluminum to form strong adhesive interphase boundaries. For example, transition metal aluminides of the Al ₃ Fe type are suitable for this purpose, since the atoms contained in them, according to phase equilibrium diagrams, can interact with the surrounding Al and Sn phases to establish strong adhesive bonds.

The specified approach was tested on the example of the Al-Sn-Fe powder system. The sintered composites of this system demonstrated good wear resistance during dry friction on a steel counterbody, high mechanical properties, and the material declared in the patent [5] was chosen as a prototype. The source of refractory solid particles in this material were iron powders, which were introduced into a mixture of elemental Al and Sn powders. During sintering, aluminum atoms diffused into the iron powders and formed a layer of reaction products from the refractory intermetallic compound Al ₃ Fe. As the layer grew, it cracked, and in place of the iron powder particles there remained agglomerates of small Al ₃ Fe particles cemented with tin. That is, the particles of the solid phase are distributed unevenly throughout the volume of the sintered composite in the form of compact clusters.

The procedure for obtaining the composite is also complicated by the need to maintain the sintered compacts at a relatively low temperature in order to complete the alloying processes between aluminum and iron in order to form a large number of Al ₃ Fe particles capable of forming a framework that supports the shape of the compact when the aluminum matrix melts during liquid-phase sintering.

In order to avoid non-uniform distribution of components in sintered composites of the Al-Fe-Sn system and reduce the time of their production, the authors propose to use ready-made powders of the Al ₃ Fe compound instead of iron powders. Presses from such mixtures with a sufficient amount of solid refractory particles can be immediately heated to a temperature above the melting point of aluminum, without waiting, as in the prototype, for the end of the alloying reaction between aluminum and iron.

The minimum amount of Al ₃ Fe particles that allows sintered compacts to retain their given shape is easily determined experimentally by heating samples above the melting point of aluminum. The maximum amount of solid particles in antifriction composites is determined by the combination of their mechanical and tribotechnical properties. A large amount of liquid phase formed during melting of Al allows obtaining materials with low residual porosity, which can be removed by simply compressing the samples in a closed press mold, without resorting to methods of intensive plastic processing such as rolling or extrusion.

The invention is illustrated by figures 1-4.

Fig. 1 shows a photograph of the original Al ₃ Fe powder.

Fig. 2 shows photographs of the structure of sintered and subsequently compacted Al-Fe-Sn composites with different contents of Al ₃ Fe particles (% by weight): 17 (a); 24 (b); 30 (c); 36 (d). Sintering temperature - 710°C. Holding time - 60 min. Light phase - tin.

Fig. 3 shows the compression curves of the claimed Al-Fe-Sn composites, the structure of which is shown in Fig. 2, as well as their analogues.

Fig. 4 shows images of the structure under the friction surface of composites 2(a, b), 3(c), 4(d) and 5(d), as well as the friction surface of composite 2(e). Sintering temperature: 620°C (a), 710°C (b-e). Pressure – 5 MPa. Sliding speed – 0.6 m/s, friction path – 1000 m.

The invention is carried out as follows.

First, briquettes for hot pressing in a closed die are obtained by sintering. For this, tin powders of grade PO 2 in an amount of tin from 37 to less than 37.7 or from more than 37.7 to 38 wt.%, ground initial powders Al ₃ Fe (Fig. 1) in an amount of 17-36 wt.% and aluminum powders of grade ASD-4 - the rest, were mixed until a homogeneous state, and then briquettes with a porosity of 8-12% were pressed from them. The briquettes were placed in a furnace with a non-oxidizing atmosphere, heated to 710-720 ° C and held for 60 minutes.

During sintering of briquettes with a higher initial porosity, their significant and uneven shrinkage was observed, leading to a significant distortion of the shape and size of the compacts and deterioration of their surface quality. In dense compacts with a porosity of < 8%, many closed pores are formed, filled with gases captured from the atmosphere. During liquid-phase sintering, the gas compressed in the pores prevents shrinkage of the samples. As a result, after sintering, the material contained many large residual pores, significantly reducing its strength and plasticity. After sintering of briquettes with optimal initial porosity, the pores in them were small and uniformly distributed throughout the volume of the sample, their volume fraction in the samples did not exceed 3-5%. Only samples of alloy No. 1 were not subjected to further compaction to a porosity of 1%, since they lost their shape during sintering due to an insufficient volume fraction of solid particles in them.

When aluminum powders melt, liquid aluminum begins to mix with liquid tin surrounding the Al ₃ Fe particles. At this time, the shape of the compacts is supported by a framework formed from particles of the refractory phase. When the particle content is less than 17% by weight, the sintered briquette loses its shape and melts.

During holding at 710-720ºС, the particles constituting the framework slightly dissolve in the surrounding melt, disengage and acquire the ability to rearrange under the influence of capillary forces. The porosity of the composites decreases, and the adhesion of the phases and the structure of the interphase boundaries improve. The said recrystallization of Al ₃ Fe particles through the liquid phase is accompanied by their enlargement and weakening of the framework they form, therefore the sintering temperature of the samples with a minimum iron aluminide content of 17% by weight was limited to 710-720ºС and a holding time of 60 minutes. Exceeding the said sintering parameters led to distortion of the shape of the compacts and their melting.

Since the shrinkage of the sintered samples was controlled by slow diffusion processes of "dissolution-precipitation", it did not ensure complete elimination of pores in a reasonable sintering time. Residual pores significantly reduced the plasticity and strength of the composites. To eliminate them, the sintered samples were placed in a press mold and heated to 250-260 ºС, and then pressed at a pressure of 305-350 MPa, during which the pores were compressed and filled with liquid tin, which improved the plasticity of the composite. After compaction, the material became more plastic and could be subjected to large deformations, leading to its strong strengthening. The achieved values of σ _0.2 and σ _B during compression of composites with different compositions are given in Table 2, and their flow curves are shown in Fig. 3.

Table 2. Mechanical and tribological properties of sintered Al-Fe-Sn composites and their prototype after hot pressing (HP) in a closed die.

Compound Receiving mode:
°C; hour Fur. properties Wear intensity, (µm/m)/
Coefficient of friction (µ) σ _0.2 ,
MPa σ _B ,
MPa δ,
% Pressure P, MPa 1 3 4 5 2 620;1 h +GP 127 156 6 0.12 0.18 0.21 0.23 710;1 h +GP 109 137 13 0.11 0.15 0.16 0.19 3 710;1 h +GP 112 142 15 0.11 0.17 0.18 0.21 4 710;1 h +GP 120 159 15 0.10 0.14 0.16 0.19 5 710;1 h +GP 144 179 11 0.06 0.26 0.29 0.30 Prototype RU 2789324 2 620;1 h + GP 93 123 24 0.13/0.55 0.19/0.35 0.23/0.32 0.24/0.29 710;1 h + GP 84 122 26 0.12/0.52 0.17/0.36 0.21/0.34 0.22/0.32 3 710;1 h + GP 110 134 20 0.11 0.17 0.20 0.23 4 710;1 h + GP 118 136 6.5 0.10 0.15 0.16 0.20 5 710;1 h + GP 134 165 5.5 0.13 0.19 0.26 0.28

The flow curves σ(δ) shown in Fig. 3 have the same structure: a short section of linear hardening is followed by a section of parabolic hardening, during which the rate of strain hardening of the material gradually decreases and stabilizes at the point σ _B at the maximum value of σ. It is followed by a short section where σ(δ) = σ _B , and then a long flat section of material softening. The maximum strength of compressible samples is achieved when they are compressed by δ = 8-13%. The rate of strain hardening of composite samples increases with an increase in the concentration of solid particles in them, and the achieved value of σ _B is also higher. Since only the grains of the aluminum matrix can be hardened in the studied composites, this means that with an increase in the concentration of solid particles, the volume fraction of the aluminum phase decreases, and with an equal value of sample settlement δ, its grains experience greater deformation. From the given compression curves σ(δ) it also follows that as a strengthening treatment it is sufficient to subject the studied composites to compression by 4-6%. As a result, the material is greatly strengthened, only slightly short of reaching σ _B , but at the same time it still retains a small reserve of plasticity.

It follows from the table that after additional pressing, the composite sintered at 710°C demonstrates better plasticity than the composite sintered at a temperature below the melting point of aluminum. This is due to the fact that the material sintered at 710°C has lower porosity, and during additional pressing in a closed die it experienced less deformation, which means that the thinning of the intergranular layers was less. And since the plasticity resource of the layers depends on their thickness, it is natural that a high sintering temperature of the composite has a favorable effect on its plasticity. In turn, high plasticity with equal strength contributes to an increase in the wear resistance of the material, since wear particles are formed after large deformations of the surface layer. This is clearly seen from Table 2, and in the photo of the structure of the near-surface layer in Fig. 4.

The photograph of the structure under the friction surface shows that before the formation of wear particles, the matrix grains undergo a large deformation - they stretch in the direction of sliding of the steel disk and become thinner in the perpendicular direction, so that their boundaries become parallel to the friction surface. The Al ₃ Fe particles are squeezed between the approaching and strengthening grains, they gradually collapse and become smaller. The tin layers squeezed between the grains are also stretched and become thinner. That is, near the friction surface, the structure of the composites changes and more closely resembles a layered structure. Upon reaching a critical deformation value, the grains begin to peel off from the friction surface, and the layering passes through the tin layers that have exhausted their plasticity resource. In place of the peeled grains, depressions filled with small particles of oxides and aluminides are formed on the friction surface (Fig. 4b).

Thus, Al ₃ Fe particles restrain the approach of deformable grains and slow down their delamination, but after the removal of the upper layer of grains they appear on the friction surface and perceive the external load. In this case, they are held on the friction surface by a viscous layer of tin. When there are many particles in the composite, not all particles are surrounded by tin, and such particles are weakly held on the friction surface. The wear intensity of the composite with a large number of hard particles increases (Table 2).

Examples of specific implementation.

Example 1

For example 1, the composition of the powder mixture indicated in Table 1 under number 2 was used.

Tin powders of grade PO 2 in the amount of 38% by weight, ground powders of Al3Fe in the amount of 17% by weight and aluminum powders of grade ASD-4 - the rest, were mixed until homogeneous, and then pressed from them into briquettes with a porosity of 8-12%. The briquettes were placed in a furnace with a non-oxidizing atmosphere, heated to 710 °C and held for 60 minutes. Then they were subjected to hot additional pressing at 250 °C in a closed press mold in order to increase their density and mechanical properties. The compaction pressure was 305 MPa. Then additional compaction of the briquette was carried out to a porosity of 1%.

Next, rectangular samples of 5x5x10 mm in size were cut from the obtained composite material for compression testing and for wear resistance during dry friction on a disk made of hardened grade 40X steel using the “pin-disk” scheme. The values of mechanical and tribotechnical properties of the composites obtained during the tests are listed in Table 2.

Examples 2-4

For examples 2-4, the powder mixture compositions indicated in Table 1 under numbers 3, 4, 5 were used. Examples 2-4 were carried out similarly to example 1.

The differences between examples 2-4 were the implementation of technological operations according to the parameters of the modes declared in the image formula within the limits.

Similar to example 1, tests of the obtained composite materials were carried out according to examples 2-4, the results of which are presented in table 2.

From the data provided in Table 2 it follows that while maintaining the volume fraction of tin in sintered composites of the Al-Fe-Sn system at 20%, their strength increases with an increase in the iron concentration, while their plasticity remains almost unchanged and remains at a level of 11-15%. Whereas the strength of the prototype also increased with an increase in concentration, their plasticity quickly decreased.

In addition to strength and plasticity, an important characteristic of bearing materials is their ability to resist abrasion during frictional contact with a steel counterbody. The fastest comparative results on their wear resistance are obtained with dry friction, carried out under identical external conditions. For example, this can be done using the "pin-disk" test scheme, which has become widespread due to the simplicity of its implementation. Tests according to this scheme were carried out at the same sliding speed (0.6 m/s) and pressure (1-5 MPa) as the prototype tests. The friction track radius and the dimensions of the tested samples were also identical. The obtained results on the wear resistance of sintered composites of the Al-Fe-Sn system are given in Table 2.

The results presented here show that, at a fixed optimum tin content, an increase in the iron aluminide concentration above 17% by weight leads to a smooth increase in the wear resistance of the composites over the entire range of pressures studied, and only at a concentration of 38% and above does the wear resistance begin to decrease. A subsequent increase in the concentration of Al ₃ Fe particles worsens the ability of the composites to resist abrasion during dry friction against a steel counterbody.

The wear rate of the Ih samples taken as a prototype changed in a similar manner. The value of Ih for composition 2 was significantly higher than that of the claimed composite with the same iron content, but as the concentration of Al ₃ Fe particles increased, it rapidly decreased, and the wear rate of the composition 4 samples was practically the same, regardless of the method of their production (Table 2). The wear resistance of the composition 5 samples began to deteriorate in both cases, but that of the prototype was higher than that of the claimed composite.

Thus, the composites obtained by the proposed method demonstrate higher strength in the entire studied range of iron concentrations compared to the prototype samples of the same composition. Their plasticity at high iron concentrations is also better than that of the prototype. The wear resistance of the composites alloyed with Al ₃ Fe particles is also higher than the wear resistance of the prototype samples with the same composition until the concentration of solid particles exceeds 38% and the number of brittle contacts between particles reaches a significant value.

Claims (9)

1. A wear-resistant antifriction composite material based on aluminum, containing tin and iron aluminide, characterized in that it contains components in the following ratio, wt.%: tin from 37 to less than 37.7 or from more than 37.7 to 38; _Al3Fe17-36 ; aluminum - the rest. 2. A method for producing a wear-resistant antifriction composite material based on aluminum, including preparing a mixture of aluminum, tin and iron powders, forming a compact, sintering it and then compacting it, wherein the compact is sintered at a temperature of 710-720°C with holding at the specified temperature, and compaction is carried out in a closed die at a temperature of 250-260°C and a pressure of 305-350 MPa, whereby a material is obtained containing components in the following ratio, wt.%: tin from 37 to less than 37.7 or from more than 37.7 to 38; _Al3Fe17-36 ; aluminum - the rest. 3. The method according to paragraph 2, characterized in that the formation of the pressing is carried out until the porosity is 8-12%.