This article deals with the fatigue properties of newly used AlZn10Si8Mg aluminium alloy where the main aim was to determine the
fatigue strength and compare it with the fatigue strength of AlSi7Mg0.3 secondary aluminium alloys which is used in the automotive
industry for cyclically loaded components. AlZn10Si8Mg aluminium alloy, also called UNIFONT 90, is self-hardening (without heat
treatments), which contributes to economic efficiency. This is one of the main reasons why is compared, and may be an alternative
replacement for AlSi7Mg0.3 alloy which is heat treated to achieve required mechanical properties. The experiment results show that the
fatigue properties of AlZn10Si8Mg alloy are comparable, if not better, than AlSi7Mg0.3 alloy. Fatigue properties of AlZn10Si8Mg alloy
are achieved after seven days of natural ageing, immediately after casting and achieving value of fatigue strength is caused by structural
components formed during solidification of the melt.
Secondary or multiple remelted alloys are common materials used in foundries. For secondary (recycled) Al-Si-Cu alloys, the major problem is the increased iron presence. Iron is the most common impurity and with presence of other elements in alloy creates the intermetallic compounds, which may negatively affect the structure. The paper deals with effect of multiple remelting on the microstructure of the AlS9iCu3 alloy with increased iron content to about 1.4 wt. %. The evaluation of the microstructure is focused on the morphology of iron-base intermetallic phases in caste state, after the heat treatment (T5) and after natural aging. The occurrence of the sludge phases was also observed. From the obtained results can be concluded that the multiple remelting leads to change of chemical composition, changes in the final microstructure and also increases sludge phases formation. The use of heat treatment T5 led to a positive change of microstructure, while the effect of natural aging is beneficial only to the 3rd remelting.
The paper deals with problems related to application of aluminum-silicon alloys for combustion engine cylinder liners
The main reason of a cavitational destruction is the mechanical action of cavitation pulses onto the material’s surface. The course
of cavitation destruction process is very complex and depends on the physicochemical and structural features of a material. A resistance
to cavitation destruction of the material increases with the increase of its mechanical strength, fatigue resistance as well as hardness.
Nevertheless, the effect of structural features on the material’s cavitational resistance has been not fully clarified. In the present paper,
the cavitation destruction of ZnAl4 as cast alloy was investigated on three laboratory stands: vibration, jet-impact and flow stands.
The destruction mechanism of ZnAl4 as cast alloy subjected to cavitational erosion using various laboratory stands is shown in the present
paper.
An understanding of the fundamental correlation between grain size and material damping is crucial for the successful development of structural components offering high strength and good mechanical energy absorption. With this regard, we fabricated aluminum sheets with grain sizes ranging from tens of microns down to 60 nm and investigated their tensile properties and mechanical damping behavior. An obvious transition of the damping mechanism was observed at nanoscale grain sizes, and the underlying causes by grain boundaries were interpreted.
Manganese is an effective element used for the modification of needle intermetallic phases in Al-Si alloy. These particles seriously
degrade mechanical characteristics of the alloy and promote the formation of porosity. By adding manganese the particles are being
excluded in more compact shape of “Chinese script” or skeletal form, which are less initiative to cracks as Al5FeSi phase. In the present
article, AlSi7Mg0.3 aluminium foundry alloy with several manganese content were studied. The alloy was controlled pollution for achieve
higher iron content (about 0.7 wt. % Fe). The manganese were added in amount of 0.2 wt. %, 0.6 wt. %, 1.0 wt. % and 1.4 wt. %. The
influence of the alloying element on the process of crystallization of intermetallic phases were compared to microstructural observations.
The results indicate that increasing manganese content (> 0.2 wt. % Mn) lead to increase the temperature of solidification iron rich phase
(TAl5FeSi) and reduction this particles. The temperature of nucleation Al-Si eutectic increase with higher manganese content also. At
adding 1.4 wt. % Mn grain refinement and skeleton particles were observed.
This paper deals with influence on segregation of iron based phases on the secondary alloy AlSi7Mg0.3 microstructure by chrome. Iron is
the most common and harmful impurity in aluminum casting alloys and has long been associated with an increase of casting defects. In
generally, iron is associated with the formation of Fe-rich phases. It is impossible to remove iron from melt by standard operations, but it is
possible to eliminate its negative influence by addition some other elements that affect the segregation of intermetallics in less harmful
type. Realization of experiments and results of analysis show new view on solubility of iron based phases during melt preparation with
higher iron content and influence of chrome as iron corrector of iron based phases. By experimental work were used three different
amounts of AlCr20 master alloy a three different temperature of chill mold. Our experimental work confirmed that chrome can be used as
an iron corrector in Al-Si alloy, due to the change of intermetallic phases and shortening their length.
Al-enriched layer was formed on a magnesium substrate with use of casting. The magnesium melt was cast into a steel mould with an
aluminium insert placed inside. Different conditions of the casting process were applied. The reaction between the molten magnesium and
the aluminium piece during casting led to the formation of an Al-enriched surface layer on the magnesium substrate. The thickness of the
layer was dependent on the casting conditions. In all fabricated layers the following phases were detected: a solid solution of Mg in Al,
Al3Mg2, Mg17Al12 and a solid solution of Mg in Al. When the temperature of the melt and the mould was lower (variant 1 – 670o
C and 310 o
; variant 2 – 680o
C and 310o
C, respectively) the unreacted thin layer of aluminium was observed in the outer zone. Applying higher
temperatures of the melt (685o
C) and the mould (325o
C) resulted in deep penetration of aluminium into the magnesium substrate. Areas
enriched in aluminium were locally observed. The Al-enriched layers composed mainly of Mg-Al intermetallic phases have hardness from
187-256 HV0.1.
The present research was conducted on thin-walled castings with 5 mm wall thicknesses. This study addresses the effect of the influence of
different master alloys, namely: (1) Al-5%Ti-1%B, (2) Al-5%Ti and (3) Al-3%B, respectively on the structure and the degree of
undercooling (ΔTα = Tα-Tmin, where Tα - the equilibrium solidification temperature, Tmin - the minimum temperature at the beginning of
α(Al) solidification) of an Al-Cu alloy. The process of fading has been investigated at different times spent on the refinement treatment ie.
from 3, 20, 45 and 90 minutes respectively, from the dissolution of master alloys. A thermal analysis was performed (using a type-S
thermocouple) to determine cooling curves. The degree of undercooling and recalescence were determined from cooling and solidification
curves, whereas macrostructure characteristics were conducted based on a metallographic examination. The fading effect of the refinement
of the primary structure is accompanied by a significant change in the number (dimension) of primary grains, which is strongly correlated
to solidification parameters, determined by thermal analysis. In addition to that, the analysis of grain refinement stability has been shown
with relation to different grain refinements and initial titanium concentration in Al-Cu base alloy. Finally, it has been shown that the
refinement process of the primary structure is unstable and requires strict metallurgical control.
This study presents an analysis of aluminium cast iron structure (as-cast condition) which are used in high temperatures. While producing casts of aluminium iron, the major influence has been to preserve the structure of the technological process parameters. The addition of V, Ti, Cr to an Fe-C-Al alloy leads to the improvement of functional and mechanical cast qualities. In this study, a method was investigated to eliminate the presence of undesirable Al4C3 phases in an aluminium cast iron structure and thereby improve the production process. V and Ti additions to aluminium cast iron allow the development of FeAl - VC or TiC alloys. In particular, V or Ti contents above 5 wt.% were found to totally eliminate the presence of Al4C3. In addition, preliminary work indicates that the alloy with the FeAl - VC or TiC structure reveals high oxidation resistance. The introduction of 5 wt.% chromium to aluminium cast iron strengthened the Al4C3 precipitate. Thus, the resultant alloy can be considered an intermetallic FeAl matrix strengthened by VC and TiC or modified Al4C3 reinforcements.
The paper deals with the influence of manganese in AlSi7Mg0.3 alloy with higher iron content. Main aim is to eliminate harmful effect of intermetallic – iron based phases. Manganese in an alloy having an iron content of about 0.7 wt. % was graded at levels from 0.3 to 1.4 wt. %. In the paper, the effect of manganese is evaluated with respect to the resulting mechanical properties, also after the heat treatment (T6). Morphology of the excluded intermetallic phases and the character of the crystallisation of the alloy was also evaluated. From the obtained results it can be concluded that the increasing level of manganese in the alloy leads to an increase in the temperature of the β-Al5FeSi phase formation and therefore its elimination. Reducing the amount of β-Al5FeSi phase in the structure results in an improvement of the mechanical properties (observed at levels of 0.3 to 0.8 wt. % Mn). The highest addition of Mn (1.4 wt.%) leads to a decrease in the temperature corresponding to the formation of eutectic silicon, which has a positive influence on the structure, but at the same time the negative sludge particles were also present
The paper deals with squeeze casting technology. For this research a direct squeeze casting method has been chosen. The influence of process parameters variation (casting temperature, mold temperature, pressure) on mechanical properties and structure will be observed. The thicknesses of the individual walls were selected based on the use of preferred numbers and series of preferred numbers (STN ISO 17) with the sequence of 3.15, 4.00, 5.00, 6.00 and 8.00 mm. The width of each wall was 22 mm with a length of 100 mm. As an experimental material was chosen the AlSi12 and AlSi7Mg0.3 alloys. The mechanical properties (UTS, E) for individual casting parameters and their individual areas of different thicknesses were evaluated. In the structure the influence of pressure on the change of the eutectic morphology, the change of the volume of eutectic and the primary alpha phase, the effect of the pressure on the more fine-grain and the regularization of the structure were evaluated.