Aluminium sheet for high temperature soldering with high strength and excellent corrosion characteristics

FIELD: metallurgy.

SUBSTANCE: invention relates to sheets from aluminium alloys for high temperature soldering, which can be used for the production of radiators. A sheet consists of a core made from an aluminium alloy and a clad material applied to at least one side of the core and made from an aluminium alloy with a lower potential than that of the core material; with that, the clad material represents the outermost layer of the sheet for high temperature soldering and is made from an aluminium alloy containing the following, wt %: 0.8 to 1.3 Mg, 0.5 to 1.5 Si, 1.0 to 2.0, preferably 1.4-1.8 Mn, ≤0.7 Fe, ≤0.1 Cu, and ≤4 Zn, ≤0.3 each of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and ≤0.5 of the sum of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the rest are Al and inevitable impurities.

EFFECT: invention allows creating thin sheets from the aluminium alloy, which have high strength, good corrosion resistance and pressure processibility.

28 cl, 3 dwg, 7 tbl, 2 ex

 

Area of technology

The present invention relates to a brazing sheet of aluminum alloy with high strength and excellent corrosion characteristics.

Background of the invention

The reduction in wall thickness from the materials of the tubes of radiators imposes stringent demands on the mechanical properties of materials, internal and external corrosion characteristics and the compatibility between the various components in the radiator when the exposure operation high temperature soldering close to the melting point of aluminum.

Previous attempts have been made to improve the corrosion resistance of brazing sheets by adding Zn and Mg to the plating side of the cooling liquid or the plating of water. The prior art has focused on the influence of Mg on the strength, and Zn were added in large quantities to ensure the effect of expendable protective anode. It was found that Zn in large quantities is undesirable, as in the case of materials, thinner tubes and depending on the operation high temperature solder of Zn can diffuse too deeply into the core, and consequently, the corrosion resistance of brazing sheet will deteriorate, causing premature leakage and failure to�echnolo product.

US7387844 discloses a brazing sheet having a consumable material plating from 2 to 9 weight % of Zn, at least one component selected from the group consisting of from 0.3 to 1.8 weight % Mn and from 0.04 to 1.2 weight % Si, and at least one component selected from the group consisting of from 0.02 to 0.25 weight % of Fe, 0.01 to 0.30 weight % of Cr, 0.005 to 0.15 weight % of Mg and 0.001 to 0.15 weight % Cu. This plating material does not provide adequate strength and corrosion resistance for a thin sheet to high-temperature soldering. The object of the present invention is to provide a thin brazing sheet of aluminum alloy, which has high strength and good corrosion resistance on the side of its inner surface which is in contact with the cooling fluid (e.g. water) being used as a tube or as a plate collector, for example, for heat exchangers such as a radiator or heater. The object of the invention is the creation of thin sheet material for brazing, which has good machinability pressure and can be used in situations for tough corrosive environment at the same time with internal and external parties, and it is considerable� prolong the service life, excluding premature leakage and failure.

Summary of the invention

The present invention relates to an aluminum brazing sheet, which comprises the core material and the plating material formed on one surface of the core material, wherein the material of plating is made of aluminum alloy consisting of 0.2 to 2.0 wt% Mg, preferably from 0.7 to 1.4 wt.% Mg, most preferably of 0.8-1.3 wt.% Mg, from 0.5 to 1.5 wt.% Si, 1.0 to 2.0 wt.%, preferably from 1.4 to 1.8 wt.% Mn, ≤0.1 wt.% Cu and ≤4 wt.% Zn, ≤0.3 wt.% each of Zr, Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder being Al and inevitable impurities.

Detailed description

It was found that the brazing sheet, such as disclosed in US7387844 (as mentioned above), has a Mg content which is not sufficient to produce the desired strength and corrosion resistance. The presence of Cr, Cu and high Zn content makes the material unsuitable as plating water side. Zn at high levels will reduce the melting point of the plating and has the potential to make the material more brittle, causing problems during rolling.

The brazing sheet of the present invention includes a core of aluminum alloy, and�euwww on one surface plating, which will be directed towards the coolant heat exchanger made of this sheet for high temperature soldering, and not necessarily having a plating of brazing alloy on the other surface. Plating side coolant hereinafter referred to as plating water side, and this plating is the most external layer of the brazing sheet, which is in direct contact with the cooling fluid.

Material plating water side is made of aluminum alloy with a lower corrosion potential than that of the core material, and represents the most external layer of the water side of the sheet for brazing. Material plating water side is made of aluminum alloy consisting of from 0.2 to 2.0 wt.% Mg, from 0.5 to 1.5 wt.% Si, 1.0 to 2.0 wt.%, preferably 1.4 to 1.8% of Mn, ≤0.7 wt.% Fe, ≤0.1 wt.% Cu and ≤4 wt.% Zn, ≤0.3 wt.% each of Zr, Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder being Al and inevitable impurities.

The plating material may preferably be made of aluminum alloy consisting essentially of from 0.7 to 1.4 wt.% Mg, from 0.5 to 1.5 wt.% Si, from 1.4 to 1.8 wt.% Mn, ≤0.7 wt.% Fe, ≤0.1 wt.% Cu and ≤4 wt.% Zn,≤0.3 wt.% each of Zr, Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder being Al and inevitable �remesi.

Material plating water side can also be made of aluminum alloy consisting essentially of from 0.8 to 1.3 wt.% Mg, from 0.5 to 1.5 wt.% Si, from 1.4 to 1.8 wt.% Mn, ≤0.7 wt.% Fe, ≤0.1 wt.% Cu and ≤4 wt.% Zn, ≤0.3 wt.% each of Zr, Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder being Al and inevitable impurities. The plating material may contain ≤0,05-0,3 wt.% Zr.

Manganese (Mn) is an element that improves the strength of the material of plating water side, as well as resistance to erosion corrosion, for example, being used as a tube in the heat exchanger. When the content of Mn is less than 1.0 wt.%, sufficient due to dispersed particles of hardening of the amount of Mn can be obtained, and the number of particles for high resistance to erosion corrosion is too small, and the strength cannot be ensured. When the content of Mn exceeds 2.0 wt%, deteriorating the machinability of plating pressure and can result in too large intermetallic particles, which could have a negative impact on fatigue properties. When the amount of Mn between the 1.4 and 1.8 wt.% achieved the desirable content of small dispersoids (<0.5 μm) and large eutectic particles, which provides improved resistance to erosion corrosion. On�that the content of Mn in the material of plating water side is set in the range of 1.0 to 2.0, more preferably from 1.4 to 1.8 wt.%.

Silicon (Si) increases the strength of the material of plating water side of the reaction with Mn. When the Si content is less than 0.5 wt.%, the number of the formed dispersoids AlMnSi is not enough and the increase in strength is not sufficient. Si also lowers the melting point of the plating, and therefore should be limited to 1.5 wt.%. Therefore, the Si content in the material of plating water side set in a range from 0.5 to 1.5%.

When the Si content is reduced, it has such an influence on the corrosion potential, the plating becomes more "noble", thereby achieving a weaker effect of anodic protection, which is undesirable. The Si content in the plating water side must also be balanced with the Si content in the core to obtain the desired effect of anodic protection. When the content of Mn is high (1,4-1,8%), the plating material may be larger than Si, because some part of Si is lost by diffusion into the core, and reacts with Mn in the formation of AlMnSi particles.

During the high temperature brazing Si also diffuses from plating water side to the core and forms dispersoid AlMnSi phase, so corrosion is localized only in the very outer layer of the core.

Zinc (Zn) is added to �the material of plating for to make a low corrosion potential of the material of plating. In the case where the Cu content in the material of plating is on the level of impurities can be achieved a sufficient effect of anodic protection and corrosion resistance can be maintained even if the Zn content in the material of plating is less than 4 wt.%. When decreasing the thickness of the core material or a high temperature brazing process or the residence time at high temperature is long, and Zn in the plating aqueous side tends to diffuse deeply into the heart, which may lead to deterioration of corrosion properties of the brazing sheet. Therefore, the upper limit of the content of Zn was set at 4 wt.%, moreover, the Zn content is preferably ≤1.4 wt.%, more preferably ≤1.1 wt.%, most preferably ≤0.4 wt.%.

Magnesium (Mg) is added to the material of plating to increase strength and to improve resistance to corrosion and erosion. When the Mg content is less than 0.2 wt.%, the effect on corrosion and strength are insufficient. If the Mg content exceeds 2.0%, the workability during rolling becomes difficult and decreases the melting point. If the Mg content is between 0.7 to 1.4 wt.%, more preferably 0.8 to 1.3 percent, above are satisfied�specified criteria for strength and workability, as well as improving the corrosion properties. A layer of plating for corrosion protection with the use of 0.8-1.3 wt.% Mg gives the optimal characteristics of the alloy core. When the content of Mg is lower than 0.8 wt.% resistance to pitting corrosion, especially in more acidic test solution with OY-water decreases so that it becomes less pronounced favourable condition with a shallow surface corrosion. Magnesium content preferably should be maintained at 1.3 wt.% or below to avoid the formation of anode Al3Mg2 particles or Al8Mg5 at the grain boundaries at temperatures above 70°C, thereby eliminating the danger of intergranular corrosion (IGC), which is harmful to aluminum. Magnesium content of more than 1.3 wt.% in the alloy plating may reduce the workability during hot rolling during the operation of connection of the core and alloy plating. Furthermore, when the magnesium content of more than 1.3 wt.% in the alloy plating increases strain hardening, so that on one side of a sheet of plating could be bent during hot rolling due to uneven stress distribution over the thickness of the sheet. To improve the suitability for processing of the composition of the plating preferably contains Ni.

The content of copper (Cu) plating water side must be set low, because the�ku it degrades the corrosion resistance, as it increases the danger of pitting. Therefore, its maximum content is set at 0.1 wt.%, preferably <0.04 wt.%.

The core material of the brazing sheet of aluminum alloy contains ≤0.1 wt.% Si, preferably ≤0.06 wt.% Si ≤0.35 wt.% Mg, from 1.0 to 2.0 wt%, preferably from 1.4 to 1.8 wt.% Mn, from 0.2 to 1.0, preferably from 0.6 to 1.0 wt.% Cu, ≤0.7 wt.% Fe, ≤0.3 wt.% each of Zr, Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder consists of aluminum and inevitable impurities.

The core material preferably contains ≤0.1 wt.% Si, preferably ≤0.06 wt.% Si ≤0.35 wt.% Mg, from 1.4 to 1.8 wt.% Mn, from 0.6 to 1.0 wt.% Cu, ≤0.7 wt.% Fe, from 0.05 to 0.3 wt.% Zr, ≤0.3 wt.% each of Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder consists of aluminum and inevitable impurities. Preferably the core material and the material of plating both contain Ni.

Mn in the core increases the strength of both in solid solution and being present in the particles. When the content of Mn in the core of at least 1.0 wt.% can stand out a large number of particles during the heating and subsequent hot rolling and can be obtained a significant potential gradient between the core and the cladding water side due to the large difference between the content of Mn in solid solution after high-temperature �Aiki. The term "heating" refers to heating of the ingot prior to hot rolling at a temperature not exceeding 550°C. When the content of Mn above 2.0 wt.% during casting can form large eutectic particles, which is undesirable in the manufacture of thinner tubes. Preferably the content of Mn at the level of 1.8 wt.% or less, as formed during casting of the primary particles will be smaller. When the content of Mn between the 1.4 and 1.8 wt.% achieved the desirable content of small dispersoids and large eutectic particles.

To further increase the strength of the produce adding 0.2 to 1.0 wt.% Cu, as copper is a hardening agent in aluminum, being composed of a solid solution. In addition, expect a significant response to aging by heat treatment or during use is subjected to high-temperature soldering of the product. However, Cu increases the sensitivity to hot cracking during casting, reduces the resistance to corrosion and reduces the temperature of the solidus. The copper content of 0.6 to 1.0 is preferred in cases that require a higher strength.

The addition of zirconium (Zr) calls increased number of very small particles, which is favorable for resistance to warping. It also provides a larger grain after high-temperature p�s, what is favorable for corrosion properties. To obtain good resistance to warping and large grains may preferably be added is 0.05 to 0.3 wt.% Zr in the core and/or alloy water side.

The concentration of silicon in the core must be ≤0.1 wt.% Si, preferably ≤0.06 wt.%. It makes any corrosion leaking in the lateral direction, thereby avoiding pitting and corrosion becomes a side. At concentrations above 0.1 wt.% significantly hampered the formation of a sacrificial layer.

In the manufacture of aluminum alloy for use in brazing sheet according to the present invention, it is impossible to avoid small amounts of impurities. These impurities in the present invention is not specifically taken into account, but the amount will never exceed 0.15 wt.%. In all embodiments and examples of the present invention, the rest is aluminum.

The brazing sheet of the present invention provides high strength and excellent corrosion characteristics as plating water side, and on the side of the solder plating. Material plating water is particularly suitable for application to the material of the core as a corrosion-better� coverage thanks fitted the corrosion potential between the core and plating. The combination of alloys allows to obtain more fine tubular materials with sufficient strength and corrosion properties. The brazing sheet preferably has a thickness of 300 μm, more preferably 200 μm, and the thickness of plating water side is preferably ≤30 μm, more preferably less than 20 microns.

Very important is the careful selection of the ranges of composition for various alloying elements in the brazing sheet. Therefore, the present invention provides a means for regulating the gradients of potential and corrosion properties of the brazing sheet using the carefully chosen contents of Mg, Mn, Si, Cu, Zr, and optionally Zn. This way you can minimize the thickness of plating water side, while the high strength and high resistance to corrosion and erosion continue. It is desirable to obtain a well-balanced improved corrosion characteristics to match the external conditions such as corrosion of the situation around the vehicle exposed to de-icing salts and situations with a low quality fluids from the inner side, instead of relying only on the action of zinc in the regulation of the mechanism of corrosion of spent plating layer of water.

Within the scope of the invention may be any aluminum alloy brazing HHH-series. Thus, the thickness of the solder plating and type of plating solder used in examples of the present invention should be interpreted only as approximate.

As the core and plating water side have high contents of Mn in order to ensure high strength of the brazing sheet. Careful regulation of the difference of the content of Si in the two materials reach the potential gradient, resulting in plating water side becomes sacrificial to the core. During the high temperature brazing of silicon (Si) in the plating of water maintain the amount of dissolved Mn in the low plating water side by stabilizing and possibly the formation of new dispersoids alpha-AlMnSi, so that after brazing will be the difference in the solid solution of manganese (Mn) in the core and in the cladding water side. The low Si content in the core allows you to create high content of dissolved Mn, since most small dispersoids AlMn particles formed during processing of the sheet will dissolve during brazing. This ensures the formation of a potential gradient, a property that is insensitive to the high-temperature cycle soldering or the thickness of plating. The ratio of Si in the plating to the Si serdtsevine mostly should be at least 5:1, preferably at least 10:1. Therefore, when the thin sheet to high-temperature soldering and the more subtle planirovkoj water side of the silicon content on the water side should preferably be 0.5 wt.% or more to ensure that there is sufficient Si to maintain a high level of dispersoids alpha-AlMnSi during brazing. If necessary, the plating water side can be added Zn to further increase the potential gradient and, if desirable, to make the plating aqueous side of the sacrificial corroding faster in the surface layer. However, the present invention allows the use of low levels of zinc content in spent plating layer, reducing the negative impact of zinc diffusing deep into the core and thereby worsen the overall corrosion characteristics from the outside. Such a product with a low content of zinc is also favorable for the suitability for recycling of products of heat exchangers, and also provides an opportunity to more flexible production of different types of heat exchangers in the same furnace for high temperature Cabinet brazing (hard soldering of aluminum in a controlled atmosphere). In combination with the action of copper, maintained at very low levels in the plating odnostoronne, and high copper content in the core, it will further exacerbate the difference in corrosion potentials and thereby to improve the corrosion characteristics as well as the effect of silicon and manganese.

When plating water side add Mg, increases the strength of the plating, which contributes to the overall strength of the brazing sheet. Due to the relatively high mechanical strength of the thus-obtained plating can be maintained at a minimum total thickness of the brazing sheet. In the present invention it was also found that Mg in the plating aqueous side reduces the depth of ulcers pitting corrosion in corrosive environments.

In some embodiments, the application may deteriorate suitability for high-temperature soldering, in the system Mg. For other geometric shapes, rather than round welded tube, such as a folded tube, the presence of Mg in the plating aqueous part, perhaps, could have a negative impact on the suitability for brazing, soldering pipe joints with In-shape.

To achieve this, the present invention involves the action of multiple dopants, where an important role is played by the silicon content in the sacrificial layer, i.e. in the plating water side, and at the core, and poet� balanced so that to the high content of silicon consumed in the plating layer of the water side, in combination with a very low silicon content in the core would lead to the difference in corrosion potentials after surgery brazing. The potential gradient is mainly reached due to the differences in the content of dissolved Mn, Cu and possibly Zn (if present) between the plating and the core. The content of Si in the core and planirovkoj have been carefully chosen for optimum performance. The Si content in the core support as low as possible to avoid the formation containing alpha-AlMnSi of dispersoids during brazing. In combination with the action of copper, maintained at very low levels in the plating aqueous part, and with a high copper content in the core it will further strengthen the difference of corrosion potential and thereby to improve the corrosion characteristics as well as the effect of silicon and manganese.

In addition, plating water side has large grains and a large number of intermetallic particles, which gives it resistance to erosion by flowing liquid. This get due to the high content of Mn and the technological route. The ingot the ingot core and plating are made in a process comprising preheating after casting to not more than 550°C. Erosion properties are important for the tubes when the system has the flowing fluid, for example, as in the radiator or heater core. Plating water side of the present invention are selected especially sure that it is resistant to erosion. Resistance to erosion depends on the proportion and distribution of particle sizes; in order for the material resisted erosion, favorable in a controlled number of particles containing Al-Si-Fe-Mn. Alloy water side of the present invention is adapted area ratio of the particles. The proportion of the area in close status depends on the composition, process and high-temperature cycle soldering. This is achieved by a method of producing AlMn-sheets according to the present invention, in which the slab plating water side for rolling is produced from a melt which contains (in weight percent) of 0.5-1.5% Si, 1.0 to 2.0%, preferably 1.4 to 1.8% of Mn, From 0.2 To 2.0% Mg, ≤0,1% Cu, ≤0,7% Fe, ≤1.4% and ≤4%, preferably ≤1.4 wt.%, more preferably ≤1.1 wt.%, most preferably ≤0.4 wt.% Zn, ≤0.3 wt.% each of Zr, Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder consists of aluminum and inevitable impurities. All quantities of alloying elements in the following weight percentages. Slab for rolling prior to hot rolling is heated at a preheating temperature of less than 550°C �La regulating the number and size dispersoid particles (particles precipitated from supersaturated solid solution), after which the heated slab for rolling is subjected to hot rolling in the hot strip to a suitable size. Normal total compression during hot rolling strip water side thickness depends on the final size and thickness of plating water, but is typically >70%. The output thickness of a hot strip for plating water side is typically in the range from 25 to 100 mm. Its welded to the slab of the core, which was derived from a melt that contains <0,1%, preferably <0,06% Si, 1.0 to 2.0%, preferably 1.4 to 1.8% of Mn, ≤0,35% Mg, ≤0.2 to 1.0%, preferably of 0.6-1.0% Cu, ≤0,7% Fe, ≤0.3 wt.% each of Zr, Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder consists of aluminum and inevitable impurities. Slab plating is heated to a heating temperature less than 550°C. It is subjected to hot rolling and then cold rolling to final thickness. The roll is preferably subjected to soft annealing at final thickness. Then, the material of plating water side has after high temperature solder microstructure, including numerical density having an equivalent diameter in the range of 50-500 nm particles in the range between 0.5 and 20×105particles per mm2, preferably between 1 and 12×105particles per mm2, most preferably mejdu and 9×10 5particles per mm2, and the numerical density having an equivalent diameter in the range of >500 nm particles in the range between 1-20×103particles per mm2, preferably between 7 and 15×103particles per mm2. Most of these fine particles is created during heating prior to hot rolling. Typical conditions include high temperature soldering temperatures up 580-630°C, for example approximately 600°C, with a dwell time of 2-5 minutes, typically about 3 minutes. A description of how to measure the density of the particles shown in Example 2.

The brazing sheet may have a solder plating Al-Si deposited directly into it plating on the opposite side, and the solder plating contains 5-13 wt.% Si. When the core has a plating solder on the opposite side of the plating aqueous hand, the low silicon content in the core provides for the formation of sacrificial layer and the corrosion develops only in a lateral direction and also on the side of the solder plating. The excellent corrosion resistance of the core material was previously shown in ER. When the brazing sheet includes a solder plating, an intermediate layer on the solder side of the brazing sheet is not required, which is a pre�Modesto for economic reasons. Simplified also recycling material when you do not use an intermediate layer composition different from the composition of the core.

Corrosion protection sheet for high temperature solder, including solder plating is excellent due to the potential gradients created by both internal and external parties. On the outer surface facing the air side, sacrificial anode durable create layer during high-temperature brazing at a subsurface level. Fine particulates in the core, which contain Al, Mn and Si, are allocated near the surface of the solder plating due to inward diffusion of Si from the solder plating. This decreases the content of Mn in solid solution in this area compared with the core. At greater depths of the core, where the silicon does not react, the majority of small dispersoids AlMn particles dissolve during the brazing operation and the amount of dissolved Mn increases. This difference in the amount of dissolved Mn between sacrificial anode sub-surface layer after the brazing operation causes the potential gradient between the outer surface and the core, providing excellent corrosion characteristics.

In addition, we have optimized the process of obtaining �such a brazing sheet, to achieve the best performance of this worksheet. The ultimate profile of Mn, Cu and Si in solid solution, and hence its corrosion protection after brazing depend on the previous history sheet processing.

The ingot sheet for high temperature solder is heated only <550°C prior to hot rolling. This processing route is chosen in order to obtain the core material with a large number of Mn-containing dispersoids that are small enough to dissolve during high temperature brazing and thereby maximize the amount of Mn in solid solution. Also preferably, the condition N compared with the state of H14. It was found that the potential gradient from the outside of the solder plating is sharper when you receive the material in a state N.

Therefore, the condition of the core sheet for high temperature brazing of aluminum alloys according to the invention is preferably N, and wherein the core slab and the slab plating preferably made in a process comprising preheating after casting to no more than 550°C. Further embodiments of the present invention will be described by using an example.

EXAMPLES

Example 1

Samples A-D of the sheet material produced using the core with the composition given in the Table below . Used hot rolled material of the material of the core, which was originally plated on 10% of the thickness of the solder plating AA and 10% of the thickness of plating water side. Plating water side removed and replaced by placywkami water away from other alloys according to the formulations in Table 2. Samples A and C are comparative examples. The thickness of the package material further reduced by cold rolling in a laboratory mill to an appropriate size and was subjected to final heat treatment to the state N.

Table 1
The chemical composition of the core, in wt.%, measured by optical emission spectroscopy (OES)
SiFeCuMnMgZnZrTi
Core0,050,20,801,7<0.01 <0.010,130,03

Table 2
The chemical composition of the alloys of the water side, in wt.%, measured by OES
SampleSiFeCuMnMgZnZrTi
A0,80,2<0.011,7<0.01<0.01<0.01<0.01
B0,80,2<0.011,71,1<0.01<0.01<0.01
C0,80,2<0.011,6<0.01 2,7<0.01<0.01
D0,80,2<0.011,61,12,7<0.01<0.01

All samples were subjected to a model of high-temperature soldering in a CAB furnace batch. The leaves are placed in pairs facing each other with placywkami water side to minimize evaporation of zinc. Used thermal cycle, which included raising the temperature from room temperature to 600°C for 20 minutes, holding at the maximum temperature for 3 minutes and then cooling to 200°C for one of two different methods of cooling, see Table 3. Atmosphere during cooling was air or nitrogen (N2). Although the cooling rate is arbitrary, it is desirable that the cooling rate was high. Different combinations of materials and methods of high-temperature brazing are shown in Table 4. As already mentioned, all samples include the core, are shown in Table 1, the solder plating AA and plating water side, are shown in Table 2. The size and thickness of blokirovok was measured on the polished samples using CBE�type of optical microscopy.

Table 3
Cycles high temperature soldering
The number of the soldering cycleHeating time (min)Maximum temperature (°C)The holding time at temperature (min)The cooling rate to 200°C (°C/h)The atmosphere during cooling
I2060022,4The air
II2060021,4N2

Table 4
The combination of materials and the scheme brazing
SamplePlating water sideThe total thickness (μm)The thickness of plating water side (μm)Casinoplatinum solder (μm) The number of the soldering cycle
A1A2102211I
B1B1901910I
C1C2022011I
D1D2051912I
A2A2102211II
B2B1901910II
D2D2051912II

Characteristics of the internal corrosion was evaluated using IP�of itania in the glass. From each combination of materials prepared test samples with dimensions of 40×80 mm. They were degreased in a degreasing bath with a mild alkaline detergent (Candoclene). The reverse side was masked with adhesive tape. Four of the test piece was immersed in each glass beaker containing 400 ml of solution in OY-water. The composition OY-water represented 195 ppm Cl-, 60 ppm SO42-, 1 ppm Cu2+and 30 ppm Fe3+. She was prepared using NaCl, Na2SO4, CuCl2.2H2O and FeCl3.6H2O in demineralised water. The beaker was placed on a hot plate with a magnetic stirrer, which can be controlled timer. A temperature cycle was set at 88°C for 8 hours and room temperature for 16 hours. Stirring was applied only during the 8-hour heating periods. The test was performed over a two week period using the same test solution all through. Analyzed duplicate samples of each combination of materials. After the test, the test samples were loaded in HNO3for 10-15 minutes and washed with demineralised water. The analysis of the depth of pitting ulcers conducted using the method of microscopy according to standard ISO 11463. For a more detailed analysis of the type of corrosion and the depth of the ulcer pitting corrosion�AI investigated the cross-sectional light optical microscope. Estimated pass-through openings, if present, but any holes closer than 5 mm to the edges is ignored.

Table 5 shows the results of tests of internal corrosion. Given the number of holes (total on two test samples). Found no holes.

Table 6 shows the depth of pitting ulcers samples A1-D1 and A3-D3. Samples B1, B2, D1 and D2 are within the scope of this invention, and A1, A2 and C1 are comparative samples.

Table 5
The number of holes after a two-week test internal corrosion
SamplePlating water sideThe total thickness (μm)The thickness of plating water side (μm)The number of holes
A1A210220
B1B190190
C1C202/td> 200
D1D205190
A2A210220
B2B190190
D2D205190

Table 6
The results of the focus method in the study of the depth of pitting ulcers after a two-week test internal corrosion
SamplePlating water sideThe average depth of pitting ulcers (μm)Standard deviation (μm)
A1A11028
B1 B7820
C1C13629
D1D7011
A2A13633
B2B7017
D2D4914

As can be seen in Table 6, samples B1 and B2 have smaller ulcers pitting than A1 and A2. Samples D1 and D2 have smaller ulcers pitting than C1. It is clear that the addition of magnesium to the plating water side reduces the depth of ulcers. This is also shown in the cross sections on Figures 1 and 2, which show the materials C1 and D1 after the test internal corrosion. The potential gradient between the plating water side and the core of the present invention is sufficient to ensure that the materials and resisted the formation of through holes in the test of internal corrosion. However, corrosion resistance is much more usalive�Xia adding Mg to the plating of water. The combination of a solid core and plating water side, which increased resistance to pitting and provides material with thinner dimensions.

Profiles of corrosion potentials were measured on the material as in the state N and able H14, by plating with solder, after high-temperature Cabinet of the soldering, as described above. Measurement of corrosion potentials were performed on 6-8 depths ranging from the surface of the residual solder plating and consistently deep into the core. Samples of pickled hot solution of NaOH to different depths (the back side was masked with adhesive tape). After etching, the samples were cleaned in concentrated HNO3and washed with demineralized water and ethanol. The thickness of each sample was measured with a micrometer before and after etching to determine the depth.

Test samples are masked using masking tape on the reverse side and edges coated with nail Polish. Active area after masking was ~20×30 mm. Electrochemical measurements were performed using the logger process Solartron IMP. As reference electrode used a standard calomel electrode (SEC). The samples were immersed in the electrolyte solution SWAAT (artificial sea water (ASTM D1141, without heavy metal�s, with a pH of 2.95). At the beginning of the measurements added 10 ml of N2O2per liter of electrolyte solution. Monitored the open-circuit potential (OCP) as a function of etching depth of the samples before measurement.

Profiles of corrosion potential are shown in Figure 3. It can be seen that the material condition N gives a steeper profile of corrosion potential than the material condition H14.

Example 2

Another aspect of the present invention is the distribution area of the particles. Used for the analysis of the material composition of the core as shown in Table 1 and plating E water side of Table 7. The content of Mg is not likely to affect the particle density to a considerable extent. Bullion plating water side was heated at a temperature between 450 and 550°C and subjected to slab hot rolling with a total reduction of 90%. Slab water side welded to the ingot core; on the opposite side of the welded slab plating solder A. This package at a temperature < 550°C were subjected to hot rolling with a total reduction of 99% to 3.9 mm. Slab was further animali to the final size of 0,270 mm cold rolling. The roll was subjected to soft annealing to the state N.

Table 7
Chemical composition �melt water side, in wt.%, measured by OES
SampleSiFeCuMnMgZnZrTi
E0,90,3<0.011,6<0.011,60,1<0.01

The material of the above roll was subjected to a model of high-temperature soldering in a CAB furnace batch. Used two thermal cycles: one consisted of raising the temperature from room temperature to 610°C for 20 min, followed by exposure for 3 minutes at maximum temperature. The second thermal cycle used is similar to the previous one, but with a maximum temperature of 585°C. Cooling was carried out in an inert atmosphere at a speed of ~0,50°C/s.

To measure the density of the particles in the material are cut in longitudinal section, ND-RD (the normal direction is the rolling direction), the plane of the strip. Section mechanically polished using a slurry Struers OP-S containing silver�kidny silicon oxide with a particle size of 0.04 μm, at the last stage of cooking. The area occupied by the particles in the cross sections, measured in the unit FEG-SEM, Philips XL30S, using a system of image analysis firm Oxford Instruments, IMQuant/X.

Image for measurements were recorded in backscattering mode using detector "in the lens in the microscope. To minimize the depth information and to obtain a good spatial resolution in the image with the inverse scattering used a low accelerating voltage, 3 kV. For the detection of particles used General threshold level of gray scale. To obtain the result, which is indicative for the number and distribution of particles in the sample frame measured image was distributed in the entire cross section. The measurement was carried out in two stages. First performed on smaller dispersoid (particles with an equivalent diameter of <500 nm). Measured over 1000 dispersoids. Measured area, A, of each particle and calculate the equivalent diameter as √(4A/π). The second dimension was carried out on the components of the particles (particles with an equivalent diameter of >500 nm). The measurement was performed on the image field, covering about 80% of the thickness of plating. Analyzed 100 of these image fields.

Sample after high-temperature brazing at 610°C for 2 minutes had �isleno density dispersoids within the size range of 50-500 nm at 3.9×10 5particles per mm2. The samples after high-temperature brazing had the numerical density of constituent particles within the size range of >500 nm at the level of 1.4×104particles per mm2. Sample after high-temperature brazing at 585°C for 2 minutes they had the numerical density of dispersoids within the size range of 50-500 nm at 6.8×105particles per mm2. The samples after high-temperature brazing had the numerical density of constituent particles within the size range of >500 nm at 1×104particles per mm2.

1. Sheet for high temperature brazing of aluminum alloys, including the core material made of aluminum alloy, and the plating material deposited on at least one side of the core material and made of aluminum alloy with a lower corrosion potential than that of the core material, wherein the plating material is the outer layer of the brazing sheet, wherein the plating material is made of aluminum alloy consisting of from 0.8 to 1.3 wt.% Mg, from 0.5 to 1.5 wt.% Si, 1.0 to 2.0 wt.%, preferably 1.4 to 1.8 wt.% Mn, ≤0.7 wt.% Fe, ≤0.1 wt.% Cu and ≤4 wt.%, preferably ≤1.4 wt.%, more preferably ≤1.1 wt.%, most preferably ≤0.4 wt.% Zn, ≤0.3 wt.% each of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and �of 0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder being Al and inevitable impurities.

2. Sheet for high temperature brazing of aluminum alloys according to claim 1, wherein the plating material is made of aluminum alloy consisting essentially of from 0.8 to 1.3 wt.% Mg, from 0.5 to 1.5 wt.% Si, from 1.4 to 1.8 wt.% Mn, ≤0.7 wt.% Fe, ≤0.1 wt.% Cu and ≤4 wt.%, preferably ≤1.4 wt.%, more preferably ≤1.1 wt.%, most preferably ≤0.4 wt.% Zn, ≤0.3 wt.% each of Zr, Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder being Al and inevitable impurities.

3. Sheet for high temperature brazing of aluminum alloys according to claim 1 or 2, wherein the plating material comprises 0.05 to 0.3 wt.% Zr.

4. Sheet for high temperature brazing of aluminum alloys according to claim 1 or 2, wherein the copper content in the plating is <0.04 wt.%.

5. Sheet for high temperature brazing of aluminum alloys according to claim 1 or 2, in which the core material contains ≤0.1 wt.% Si, preferably ≤0.06 wt.% Si ≤0.35 wt.% Mg, from 1.0 to 2.0 wt%, preferably from 1.4 to 1.8 wt.% Mn, from 0.2 to 1.0, preferably from 0.6 to 1.0 wt.% Cu, ≤0.7 wt.% Fe, ≤0.3 wt.% each of Zr, Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder consists of aluminum and inevitable impurities.

6. Sheet for high temperature brazing of aluminum alloys according to claim 5, in which the core material contains ≤0.1 wt.% Si preferably ≤0.06 wt.% Si, ≤0.35 wt.% Mg, from 1.4 to 1.8 wt.% Mn, from 0.6 to 1.0 wt.% Cu, ≤0.7 wt.% Fe, from 0.05 to 0.3 wt.% Zr, ≤0.3 wt.% each of Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder consists of aluminum and inevitable impurities.

7. Sheet for high temperature brazing of aluminum alloys according to claim 3, in which the core material contains ≤0.1 wt.% Si, preferably ≤0.06 wt.% Si ≤0.35 wt.% Mg, from 1.0 to 2.0 wt%, preferably from 1.4 to 1.8 wt.% Mn, from 0.2 to 1.0, preferably from 0.6 to 1.0 wt.% Cu, ≤0.7 wt.% Fe, ≤0.3 wt.% each of Zr, Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder consists of aluminum and inevitable impurities.

8. Sheet for high temperature brazing of aluminum alloys according to claim 7, in which the core material contains ≤0.1 wt.% Si, preferably ≤0.06 wt.% Si ≤0.35 wt.% Mg, from 1.4 to 1.8 wt.% Mn, from 0.6 to 1.0 wt.% Cu, ≤0.7 wt.% Fe, from 0.05 to 0.3 wt.% Zr, ≤0.3 wt.% each of Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder consists of aluminum and inevitable impurities.

9. Sheet for high temperature brazing of aluminum alloys according to claim 4, in which the core material contains ≤0.1 wt.% Si, preferably ≤0.06 wt.% Si ≤0.35 wt.% Mg, from 1.0 to 2.0 wt%, preferably from 1.4 to 1.8 wt.% Mn, from 0.2 to 1.0, preferably from 0.6 to 1.0 wt.% Cu, ≤0.7 wt.% Fe, ≤0.3 wt.% each of Zr, Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder consists of Aluminii inevitable impurities.

10. Sheet for high temperature brazing of aluminum alloys according to claim 9, in which the core material contains ≤0.1 wt.% Si, preferably ≤0.06 wt.% Si ≤0.35 wt.% Mg, from 1.4 to 1.8 wt.% Mn, from 0.6 to 1.0 wt.% Cu, ≤0.7 wt.% Fe, from 0.05 to 0.3 wt.% Zr, ≤0.3 wt.% each of Ti, Ni, Hf, V, Cr, In, Sn and ≤0.5 wt.% the amounts of Zr, Ti, Ni, Hf, V, Cr, In, Sn, and the remainder consists of aluminum and inevitable impurities.

11. Sheet for high temperature brazing of aluminum alloys according to claim 1 or 2, wherein said material of plating is a plating water side, and wherein the core has an additional solder plating Al-Si directly deposited plating on the opposite side, and the solder plating contains 5-13 wt.% Si.

12. Sheet for high temperature brazing of aluminum alloys according to claim 11, characterized by the fact that the ratio of Si in the plating aqueous side to Si in the core is at least 5:1, preferably at least 10:1.

13. Sheet for high temperature brazing of aluminum alloys according to claim 5, in which said material of plating is a plating water side, and wherein the core has an additional solder plating Al-Si directly deposited plating on the opposite side, and the solder plating contains 5-13 wt.% Si.

14. Sheet for high temperature� brazing of aluminum alloys according to claim 13, characterized by the fact that the ratio of Si in the plating aqueous side to Si in the core is at least 5:1, preferably at least 10:1.

15. Sheet for high temperature brazing of aluminum alloys according to claim 1 or 2, wherein the thickness of the brazing sheet is less than 300 microns, preferably less than 200 microns.

16. Sheet for high temperature brazing of aluminum alloys according to claim 15, in which the thickness of plating is ≤30 microns, preferably less than 20 microns.

17. Sheet for high temperature brazing of aluminum alloys according to claim 5, in which the thickness of the brazing sheet is less than 300 microns, preferably less than 200 microns.

18. Sheet for high temperature brazing of aluminum alloys according to claim 17, in which the thickness of plating is ≤30 microns, preferably less than 20 microns.

19. Sheet for high temperature brazing of aluminum alloys according to claim 1 or 2, wherein the aluminum alloy core is in the state N.

20. Sheet for high temperature brazing of aluminum alloys according to claim 5 in which the aluminum alloy core is in the state N.

21. Sheet for high temperature brazing of aluminum alloys according to claim 1 or 2, characterized by the fact that it is made from the core and slab slab plating, over and above the core slab and the slab placerank� made in the process, comprising preheating after casting to no more than 550°C.

22. Sheet for high temperature brazing of aluminum alloys according to claim 5, characterized by the fact that it is made from the core and slab slab plating, over and above the core slab and the slab plating made in a process comprising preheating after casting to no more than 550°C.

23. Sheet for high temperature brazing of aluminum alloys according to claim 1 or 2, characterized in that the plating material has a microstructure after brazing comprising a number density with equivalent diameter in the range of 50-500 nm particles in the range between 0.5 and 20×105particles per mm2, preferably between 1 and 12×105particles per mm2, most preferably between 2 and 9×105particles per mm2, and the numerical density having an equivalent diameter in the range of >500 nm particles in the range between 1-20×103particles per mm2, preferably between 7 and 15×103particles per mm2.

24. Sheet for high temperature brazing of aluminum alloys according to claim 5, characterized in that the plating material has a microstructure after brazing comprising a number density with equivalent diameter in the range of 50-500 nm particles in the range between 0.5 and 20×105particles per mm2preferably m�waiting for 1 and 12×10 5particles per mm2, most preferably between 2 and 9×105particles per mm2, and the numerical density having an equivalent diameter in the range of >500 nm particles in the range between 1-20×103particles per mm2, preferably between 7 and 15×103particles per mm2.

25. Sheet for high temperature brazing of aluminum alloys according to claim 11, characterized in that the plating material has a microstructure after brazing comprising a number density with equivalent diameter in the range of 50-500 nm particles in the range between 0.5 and 20×105particles per mm2, preferably between 1 and 12×105particles per mm2, most preferably between 2 and 9×105particles per mm2, and the numerical density having an equivalent diameter in the range of >500 nm particles in the range between 1-20×103particles per mm2, preferably between 7 and 15×103particles per mm2.

26. Sheet for high temperature brazing of aluminum alloys according to claim 12, characterized in that the plating material has a microstructure after brazing comprising a number density with equivalent diameter in the range of 50-500 nm particles in the range between 0.5 and 20×105particles per mm2, preferably between 1 and 12×105particles per mm2most preferred�tive between 2 and 9×10 5particles per mm2, and the numerical density having an equivalent diameter in the range of >500 nm particles in the range between 1-20×103particles per mm2, preferably between 7 and 15×103particles per mm2.

27. Sheet for high temperature brazing of aluminum alloys according to claim 13, characterized in that the plating material has a microstructure after brazing comprising a number density with equivalent diameter in the range of 50-500 nm particles in the range between 0.5 and 20×105particles per mm2, preferably between 1 and 12×105particles per mm2, most preferably between 2 and 9×105particles per mm2, and the numerical density having an equivalent diameter in the range of >500 nm particles in the range between 1-20×103particles per mm2, preferably between 7 and 15×103particles per mm2.

28. Sheet for high temperature brazing of aluminum alloys according to claim 14, characterized in that the plating material has a microstructure after brazing comprising a number density with equivalent diameter in the range of 50-500 nm particles in the range between 0.5 and 20×105particles per mm2, preferably between 1 and 12×105particles per mm2, most preferably between 2 and 9×105particles per mm2, and the numerical density�there having an equivalent diameter in the range > 500 nm particles in the range between 1-20×103particles per mm2, preferably between 7 and 15×103particles per mm2.



 

Same patents:

FIELD: metallurgy.

SUBSTANCE: this process comprises casing of ingot from 6000-series aluminium alloy, it homogenisation, hot pressing at the rate of outflow of 3.0-30.0 m/min from heated container, heat treatment to solid solution by quenching in water, straightening after quenching by stretching and artificial ageing.

EFFECT: development of high-alloyed Al-Mg-Si system alloy with good mechanical, processing and antirust properties.

5 tbl, 3 dwg

FIELD: chemistry.

SUBSTANCE: invention relates to an aluminium alloy for making substrates for offset printing plates. The aluminium alloy contains the following components in wt %: 0.2% ≤ Fe≤0.5%, 0.41% ≤ Mg ≤ 0.7%, 0.05% ≤ Si ≤ 0.25%, 0.31% ≤ Mn ≤0.6%, Cu ≤0.04%, Ti ≤ 0.05%, Zn ≤ 0.05%, Cr ≤ 0.01%, the balance - Al and inevitable impurities, each present in an amount of not more than 0.05%, and making up at most 0.15%, overall.

EFFECT: aluminium alloy and an aluminium strip made from an aluminium alloy which is suitable for making substrates for printing plates, having high fatigue resistance when bent across the direction of rotation and high thermal stability without reducing granulation capacity.

7 cl, 4 tbl, 2 dwg

FIELD: metallurgy.

SUBSTANCE: invention relates to the method for manufacturing of a strip, made of alloy of Al-Mg-Si, in which a bar for rolling is cast from alloy Al-Mg-Si, exposed to homogenisation, the bar for rolling heated to temperature of hot rolling, is exposed to hot rolling and then, if required, cold rolling to its final thickness, at the same time the hot strip has temperature of not more than 130°C directly at the outlet from the last stage of hot rolling, preferably the temperature of not higher than 100°C, afterwards the strip is wound at this or lower temperature.

EFFECT: method makes it possible to perform aluminium strips from alloy Al-Mg-Si, which have higher relative extension and accordingly higher extents of deformation when structural metal sheets are made.

15 cl, 5 tbl, 4 dwg

FIELD: metallurgy.

SUBSTANCE: composite material contains copper, manganese, zirconium, iron, silicon and boron, and has a structure consisting of solid aluminium solution and phases uniformly distributed in it at their further ratio in solid solution, wt %: 6-15 B4C, 2-6 Al15(Fe,Mn)3Si2, 2-6 Al20Cu2Mn3, 0.4-0.8 Al3Zr.

EFFECT: increasing heat resistance of material to heating processes at sufficient level of mechanical properties.

2 cl, 1 tbl, 5 ex

FIELD: metallurgy.

SUBSTANCE: magnesium-containing high-silica aluminium alloys intended for use as structural materials, including shapes, bars, sheets and forged pieces, are manufactured with the help of a technological process containing the following operations: ingot casting from the alloy by method of casting into a chill mould, preliminary heating of the ingot in order to disperse particles of eutectic phase of silicon, treatment in thermoplastic condition and thermal treatment in order to produce an item of final shape and with modified microstructure. Aluminium alloys contain, wt %: 0.2-2 of magnesium and 8-18 of silicon and have homogeneous and fine-grained microstructure, at the same time the aluminium matrix is homaxonic with the average size of grain, not exceeding 6 mcm, and particles of silicon and secondary phase are dispersed at the average size of particles not exceeding 5 mcm. Without addition of any modifiers they are produced with low costs by combination of casting into a chill mould with treatment in thermoplastic condition and thermal treatment.

EFFECT: high plasticity and relatively high strength.

8 cl, 13 dwg, 10 tbl, 1 ex

FIELD: metallurgy.

SUBSTANCE: aluminium alloy contains the following components: from 4.5 to 6.5 wt % magnesium, from 1.0 to 3.0% wt % silicon, from 0.3 to 1.0% wt % manganese, from 0.02 to 0.3% wt % chromium, from 0.02 to 0.2% wt % titanium, from 0.02 to 0.2 wt % zirconium, from 0.0050 to 1.6% wt % of one or more rare-earth metals, max. 0.2% iron, and the rest is aluminium.

EFFECT: alloy has high strength properties and is intended for use in die casting and related methods.

8 cl, 1 tbl

FIELD: metallurgy.

SUBSTANCE: aluminium-based alloy contains the following, wt %: zinc - 6.35 - 8.0, magnesium - 0.5 - 2.5, copper - 0.8 -1.3, iron - 0.02 - 0.25, silicon - 0.01 - 0.20, zirconium - 0.07 - 0.20, manganese - 0.001 - 0.1, chrome - 0.001 - 0.05, titanium - 0.01 - 0.10, boron - 0.0002 -0.008, beryllium - 0.0001 - 0.05, at least one element from potassium, sodium, calcium group in quantity of 0.0001 - 0.01 each, aluminium is the rest; at total content of zinc, magnesium, copper within 8.5-11.0, and that of zirconium, manganese and chrome - within 0.1-0.35. Method involves loading and melting of charge components, flux treatment of molten metal, molten metal purification, further vacuum treatment of molten metal in mixer and casting of ingots; boron is added to molten metal in the form of Al-Ti-Be alloy which is distributed at least one hour before molten metal pouring to mixer along the whole surface area of mixer bottom; at that, mixer is pre-heated to temperature which is by 15-30°C more than molten metal temperature, and vacuum treatment of molten metal in mixer is performed at temperature of 695-720°C, during 45-90 minutes.

EFFECT: invention allows obtaining high-strength aluminium alloys with absence of primary intermetallic compounds, decreased content in them of non-metallic inclusions and dissolved gases, with stable properties and optimum size of grain on basis of standard furnace and process equipment.

2 cl, 3 tbl

FIELD: metallurgy.

SUBSTANCE: Invention relates to metallurgy and may be sued in producing strained semi-finished products from thermally non-hardenable welded aluminium-based alloys used as structural and semiconductor material, primarily, in aerospace and nuclear engineering. Aluminium-base alloy comprises the following components in wt %: magnesium - 1.8-2.4, scandium - 0.2-0.4, zirconium - 0,1-0.2, cerium - 0.0001-0.005, iron - 0.01-0.15, silicon - 0.01-0.1, aluminium making the rest. Note here that iron-to-silicon content ratio may not be less than unity.

EFFECT: higher strength and conductivity, hence, reduced weight.

2 tbl, 1 ex

FIELD: metallurgy.

SUBSTANCE: invention refers to deformed thermally hardened high-tensile aluminium alloys Al-Zn-Mg-Cu designed for fabrication of all kinds of deformed semi-finished products, including thin sheets used in aircraft and machine engineering and other branches of industry. Deformed alloy on base of aluminium and an item out of it contain the following components, wt %: zinc 2.5-4.0, magnesium 4.1-6.5, copper 0.2-1.0, iron to 0.25, silicon to 0.15, scandium 0.005-0.3, zirconium 0.005-0.25, nickel and/or cobalt to 0.1, titanium to 0.15, boron and/or carbon to 0.05, at least one element out of group: hafnium to 0.15, molybdenum to 0.15, cerium to 0.15, manganese to 0.5, chromium to 0.28, yttrium to 0.15, vanadium to 0.15, niobium to 0.15, aluminium and unavoidable impurities - the rest, also ratio of Mg contents to Zn contents is more or equal to 1.1.

EFFECT: production of alloy and items out of it possessing raised strength properties at simultaneous increased wear-resistance, reduced rate of crack growth, increased durability of welded connections and reduced density, which results in increased resource and reliability of items operation and in reduced weight of structures.

3 cl, 2 tbl, 1 ex

FIELD: metallurgy.

SUBSTANCE: alloy contains following components, wt %: magnesium 4.1-4.9, titanium 0.01-0.04, beryllium 0.0001-0.005, zirconium 0.05-0.12, scandium 0.17-0.30, cerium 0.0001-0.0009, manganese 0.19-0.35, chromium 0.01-0.05, group of elements, containing iron and silicon 0.06-0.25, aluminium is the rest, at that value of iron content relation to silicon content has to be not less than unity.

EFFECT: increased strength property, strength of welded connection at cryogenic temperatures, weight saving of welded fabrication, manufactured from suggested alloy.

2 tbl, 1 ex

FIELD: metallurgy.

SUBSTANCE: first, steel plates are covered with a lead layer, then, they are filled with a water solution of flux, moisture is removed, after that, they are collected to packs and soaked in an aluminium melt at the overheat temperature that is by 50-100°C higher than the liquidus line of aluminium alloy.

EFFECT: reduction of surface tension of aluminium melt and improving flowability of aluinium along steel, which contributes to improvement of adhesion strength of composite material layers.

1 ex

FIELD: metallurgy industry.

SUBSTANCE: invention relates to a brazing sheet of a laminated aluminium alloy and can be used in the manufacture of heat exchangers. The brazing sheet of the laminated aluminium alloy consisting of the material of the base layer, which on one or both sides has an intermediate layer composed of Al-Si brazing solder located between the base layer and a thin coating layer over the intermediate layer. And the material of the base layer and the coating layer has a higher melting point than the Al-Si brazing solder. The coating layer comprises, in weight %: Bi 0.01-1.00, Mg ≤ 0.05, Mn ≤ 1.0, Cu ≤ 1.2, Fe ≤ 1.0, Si ≤ 4.0, Ti ≤ 0.1, Zn ≤ 6, Sn ≤ 0.1, In ≤ 0.1, unavoidable impurities ≤0.05, Al - the rest.

EFFECT: brazing sheet can be soldered in an inert or reducing atmosphere without the need to use the flux that provides the strength of the brazed joint.

24 cl, 1 tbl, 7 ex

FIELD: metallurgy.

SUBSTANCE: invention relates to production of laminar composite steel-aluminium materials. Steel sheets are pre-coated with flux water solution containing KF - 36-40%; AlF3 - 44-50%; K2TiF6 - 10-20%, water is removed to pile the sheets to be impregnated with aluminium melt with overheating temperature some 50-100°C higher than aluminium melt liquidus line.

EFFECT: better adhesion between aluminium and steel, titanium alloyed transition intermetallide ply their between.

1 ex

FIELD: metallurgy.

SUBSTANCE: invention relates to an extruded or rolled clad metal product and can be used in the transport industry, aerospace products and ships. The product includes a cladded metal layer and a cladding metal layer on at least one surface of the cladded layer; with that, the cladded and the cladding metal layers are made from aluminium alloys containing the following, wt %: 3 to 8 Mg and Sc in the range of 0.05 to 1; with that, the content of Sc in the alloy of the cladded layer is lower than its content in the alloy of the cladding layer by 0.02% or more. The invention also relates to a welded structure including such a metal product.

EFFECT: as a result of use of the invention, products are made from the aluminium alloy containing Sc with an improved strength and weldability balance.

14 cl, 1 ex

FIELD: metallurgy.

SUBSTANCE: invention relates to metallurgy, and namely to two-layered flat rolled stock with thickness of 10-50 mm, which consists of a layer of wear-resistant steel and a layer of weldable steel for manufacture of weld structures subject to impact abrasive wear and operating at the temperature of up to -40°C. Wear-resistant steel contains the following, wt %: carbon 0.25-1.2, silicon 0.2-1.8, manganese 0.3-2.0, phosphorus not more than 0.025, sulphur not more than 0.025, chrome 0.3-6.5, nickel 0.03-2.0, one or more elements of the following group: molybdenum 0.2-1.5, tungsten 0.5-1.5, copper 0.05-0.4, niobium 0.01-0.1 and vanadium 0.02-0.7, and iron and inevitable impurities are the rest. Weldable steel contains the following, wt %: carbon 0.002-0.3, silicon 0.10-0.6, manganese 0.4-1.8, phosphorus not more than 0.02, sulphur not more than 0.01, chrome 0.01-0.4, nickel 0.01-0.5, one or more elements of the following group: copper 0.01-0.4, molybdenum 0.01-0.1, niobium 0.01-0.1 and vanadium 0.02-0.1, iron and inevitable impurities are the rest. Carbon equivalent of weldable steel is not more than 0.45, thickness of a layer of wear-resistant steel is 10-40% or 60-90% of total thickness of rolled stock, and adhesion strength of layers is at least 450 N/mm2.

EFFECT: after heat treatment items made from rolled stock at optimum consumption of alloy elements have high wear resistance, hardness of at least 500 HBW, high strength of a layer from weldable steel with yield point of at least 500 MPa, in a combination with good weldability and impact viscosity on a sharp notch at the temperature of up to -40°C of at least 30 J/cm2.

2 cl, 2 tbl

FIELD: process engineering.

SUBSTANCE: invention relates to production of cylindrical composite steel-aluminium materials. Cylindrical steel article with thread is pre-coated with flux containing KF 55% (mol.) and AlF3 45% (mol.) and impregnated in aluminium melt with overheating temperature 50-100°C higher than aluminium alloy liquidus line. Note here that thread pitch 0.3 mm is selected to allow a capillary filling of said thread with aluminium melt.

EFFECT: simplified and high-efficiency process.

FIELD: machine building.

SUBSTANCE: method involves production of a blank by making a package from aluminium alloy plates and intermediate layers of composite component, heating of the package and applying of compression force to it to provide for diffusion welding, afterwards the blank is subject to further processing by intensive plastic deformation by all-round forging with successive change of the deformation direction in three coordinate axes of the blank and with stepwise decrease of the deformation temperature until the accumulated deformation level in the blank volume is at least 3.

EFFECT: invention allows for the production of aluminium composite material with ultra-fine structure having improved performance characteristics.

1 ex

FIELD: metallurgy.

SUBSTANCE: alternating layers of base metal and reinforcing metal are packed at the ratio of layers area making 1:(0.5-0.7). Layers are subjected to explosion welding, low-temperature annealing, rolling and final high-temperature annealing. Used reinforcing layer is composed by perforated metal sheets with through channels uniformly distributed over sheet area. Said tapered channels feature opposite-direction taper in adjacent channels. Channels with like taper are staggered in sheet plane.

EFFECT: high modulus of elasticity, higher strength of weld, lower anisotropy of properties.

3 dwg, 1 tbl

FIELD: process engineering.

SUBSTANCE: invention relates to powder metallurgy, particularly, to materials intended for production of laminar bimetallic composites. Proposed method comprise the following steps whereat dry aluminium powder is fed to strain region between dry aluminium powder band, said band and said powder are rolled together to reduction of 30-50% to produce aluminium coat on steel strip and thermal processing is effected. After heat treatment, said steel strip with aluminium coat applied thereon is cold-rolled to final reduction of 15-25% and rolled-drawn to height reduction of 20-30%.

EFFECT: production of laminar bimetallic composites with ductility that allows high degree of straining.

1 tbl, 1 ex

FIELD: process engineering.

SUBSTANCE: invention relates to metallurgy. Proposed method comprises the following stages: hot- or cold-rolling of steel sheet including steel backing and pre-applied coating of aluminium-silicon alloy. Cutting said steel sheet in billet with said coating, heating it in protection-free atmosphere to Ti making from Tc-10°C to Tc where Tc is the said coating eutectic or solidus temperature. Heating the billet from Ti to Tm in protection-free atmosphere at heating rate V where V is rate of heating from Ti to Tt for obtaining heat billet with coating. Holding heated billet with coating at said Tt for time tm. Then billet is hot-formed to produce the part with coating and cooled down to produce microstructure in said steel backing including at least, one component selected form martensite and bainite.

EFFECT: high mechanical strength, higher resistance to lamination and corrosion.

21 cl, 6 dwg

FIELD: production of antifriction materials.

SUBSTANCE: the invention is dealt with production of antifriction materials, which are used in plain bearers. The invention offers a multilayer laminate for plain bearers with a base layer, a layer of a bearing alloy, the first interlayer made out of nickel, the second interlayer made out of tin and nickel, and also a sliding layer made out of copper and tin. At that the sliding layer(4) has a mould (5) made out of tin and including the copper-stannic particles (6) consisting by 39-55 mass % out of copper and the rest - tin. The technical result of the invention is an increase of wear-resistance of the material at an increased specific loading on it.

EFFECT: the invention ensures an increase of wear-resistance of the material at an increased specific loading on it.

9 cl, 4 dwg, 1 ex

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