Method for making articles of metallic alloy subjected to cold working (variants)

FIELD: manufacture of metallic articles, particularly of hard-to-form intermetallic alloys, possibly electric resistive heating members.

SUBSTANCE: article is made of aluminides of iron, nickel and titanium. Method comprises steps of subjecting article being cold worked to cold hardening; performing rapid annealing at seasoning less than 1 min; repeating operations of cold working and rapid annealing for receiving article with desired size. It is possible to make article by casting, powder metallurgy process or plasma deposition.

EFFECT: enhanced strength of article.

26 cl, 4 dwg

 

The technical field

The present invention in General relates to the fabrication of metal products such as sheet, strip, circular and band profile or wire, is especially difficult to handle intermetallic alloys of the type aluminum with iron, Nickel and titanium.

The level of technology

Intermetallic compounds of iron with aluminum Fe3Al, having ordered volume-centered cubic crystal structure, described in U.S. patent No. 5320802; 5158744; 5024109 and 4961903. Galatasaray disordered alloy with volumetric-centered crystal structure is described in U.S. patent No. 5238645, according to which the alloy includes 8-9,5 wt.% Al, ≤7 wt.% Cr, ≤4 wt.% Mo, ≤0,05 wt.% C ≤0.5 wt.% Zr ≤0.1 wt.% Y, preferably 4.5 to 5.5 wt.% Cr, 1.8 to 2.2 wt.% Mo, 0.02 to to 0.032 wt.% With and 0.15-0.25 wt.% Zr.

The iron-based alloys containing 3-18% Al, 0.05 to 0.5 wt.% Zr, 0.01 to 0.1 wt.% In and optional Cr, Ti and Mo are described in U.S. patent No. 3026197 and canadian patent No. 648140. In U.S. patent No. 3676109 described alloy based on iron containing 3 to 10 wt.% Al, 4-8 wt.% Cr, about 0.5 wt.% Cu, less than 0.05 wt.% C, 0.5 to 2 wt.% Ti and Mn optional and C.

Containing aluminum alloys based on iron, serving as the electrical resistance of the heating elements described in U.S. patent No. 1550508, 1990650 and 2768915 and in canadian patent No. 648141. Described in atente No. 1550508 alloys include 20 wt.% Al and 10 wt.% Mn, 12-15 wt.% Al and 6-8 wt.% Mn, 12-16 wt.% Al and 2-10 wt.% Cr. All the examples in this patent include at least 6 wt.% Cr and not less than 10 wt.% Al. Described in the patent No. 1990650 alloys include 16-20 wt.% Al, 5-10 wt.% Cr, ≤0,05 wt.% C ≤0.25 wt.% Si, 0.10 to 0.5 wt.% Ti ≤1.5 wt.% Mo and 0.41-1.5 wt.% Mn, a only shows an example includes a 17.5 wt.% Al, 8.5 wt.% Cr, of 0.44 wt.% Mn, 0.36 wt.% Ti, 0.02 wt.% With and 0.13 wt.% Si. Described in the patent No. 2768915 alloys include 10-18 wt.% Al, 1-5 wt.% Mo, Ti, TA, V, Cb, Cr, Ni, and W, and only the example consists of 16 wt.% Al and 3 wt.% Mo. Described in canadian patent alloys include 6-11 wt.% Al, 3-10 wt.% Cr, ≤4 wt.% Mn, ≤1 wt.% Si, ≤0.4 wt.% Ti ≤0.5 wt.% C, 0.2 to 0.5 wt.% Zr and 0.05-0.1 wt.% In, and only shows an example includes at least 5 wt.% Cr.

The resistive heaters of the various materials described in U.S. patent No. 5249586 and in patent applications U.S. No. 07/943504, 08/118665, 08/105346 and 08/224848.

In U.S. patent No. 4334923 described suitable for cold rolling, oxidation resistant alloy based on iron for catalytic exhaust gas containing ≤0,05%, 0,1-2% Si, 2-8% Al, 0.02 To 1 Y, <0,009% P, <0,006% S and <0,009% O.

In U.S. patent No. 4334923 described heat-resistant alloy based on iron containing 10-22% Al, 2-12% Ti, 2-12% of Mo, 0.1 To 1.2% Of Hf, ≤1.5% of Si, ≤0,3%, ≤0.2%, ≤1,0% TA, ≤0,5% W, ≤0,5% V, ≤to 0.5% Mn, ≤0,3%, ≤0,3% Nb and ≤0,2% La.

In Japanese published the Anna patent application No. 53-119721 described wear-resistant alloy with high magnetic permeability and is easy to work, containing 1.5-17% Al, 0.2 To 15% Cr and 0.01-8% other optional additives: <4% Si, <8% Mo, <8% Ti, <8% Ge, <8% Cu, <8% V <8% Mn, <8% Nb, <8% TA, <8% Ni, <8%, <3% Sn <3% Sb, <3% Be <3% Hf, <3% Zr, <0.5% of Pb and <3% rare earth metals.

Released publication in Advances in Powder Metallurgy, vol. 2 by J.R. Knibl 1990 OYe et al. "Microstructure and Mechanical Properties of P/M Fe3Al Alloys", pages 219-231, describes a method of obtaining Fe3Al containing 2 and 5% Cr, by powder metallurgy - spraying of the melt with an inert gas. To obtain sheets powders rolled into the shell of mild steel, pumped out the air and subjected to hot pressing at 1000°reducing the surface area of 9:1. The pressing was removed from the mold and was valavala at 1000°to the thickness 0,340 inch (8,64 mm), was rolled at 800°a sheet with a thickness of about 0.10 inch (2.54 mm) and finally rolled at 650°before being 0.030 inch (0.76 mm).

Released in 1991, published in Mat. Res. Soc. Symp. Proc., vol. 213, by V.K, Sikka "Powder Processing of Fe3Al-based Iron-Aluminide Alloys", pp. 901-906, describes a method of obtaining a containing 2 and 5% Cr gentoolinux powders on the basis of Fe3Al going to produce sheets. To obtain sheets powders rolled into the sheath of mild steel and subjected to hot pressing at 1000°C, reducing the surface area of 9:1. The sheath was removed, and the rods were valavala 50% at 1000°With, they rolled 50% at 850°and finally rolled to 0% at 650° With up to 0,76 mm

In article Sikka et al. "Powder Production, Processing and Properties of Fe3Al", pages 1-11, presented at the 1990 Powder Metallurgy Conference Exhibition in Pittsburgh, PA, describes a method for powder Fe3Al by melting the constituent metals in a protective atmosphere, passing the metal through a metering nozzle and atomizing the melt stream of compressed nitrogen. Of the powder has been pressed, filling the sheath of mild steel with a thickness of 76 mm, the air is evacuated from the heating for 1.5 hours at 1000°and subjecting to extrusion through a die with a diameter of 25 mm, which reduced the surface area of 9:1. Sheets of a thickness of 0.76 mm was obtained after removal of the shell, rolling to 50% at 1000°With, rolling to 50% at 850°and finish rolling at 50% at 650°C.

Dispersion-hardened oxide powders of iron-based alloys described in U.S. patent No. 4391634 and 5032190. In the first of them describes deprived of Ti alloys containing 10-40% Cr, 1-10% Al and ≤10% dispersion of oxides. The second section describes the method of producing sheets of alloy MA 956 containing 75% Fe, 20% Cr, 4.5% Of Al and 0.5% Ti and 0.5% Y2O3.

In the publication LeFort et al. "Mechanical Behavior of FeAl40Intermetallic Alloys", presented at Proceedings of International Symposium on Intermetallic Compounds - Structure and Mechanical Properties (JIMIS-6), pp. 5769-583, held in Sendai, Japan on June 17-20, 1991, describes various properties gentoolinux alloys (25 wt.% Al) with the addition of boron, zirconium, chromium and CERI is. The alloys were obtained using vacuum casting and pressing at 1100°With or molded under pressure at 1000°and 1100°C.

In the publication of D. Pocci et al. "Production and Properties of CSM FeAl Intermetallic Alloys", presented at the Minerals, Metals and Materials Society Conference (1994 TMS Conference on "Processing, Properties and Applications of Iron Aluminides", pages 19-30, held in San Francisco, California on February 27-March 3, 1994, describes various properties of the intermetallic compounds of Fe40Al in the processing of different methods, such as casting and pressing, spraying gas and pressing, machining, powder and pressing, and that mechanical treatment is used to strengthen the material finely dispersed oxides. The article argues that the resulting alloys FeAl having an ordered crystalline structure B2 containing from 23 to 25 wt.% Al (atomic concentration of about 40%) and alloying elements Zr, Cr, CE, s, and Y2O3.

In the publication J.H. Schneibel "Selected Properties of Iron Aluminides", pages 329-341, presented at the TMS Conference in 1994, describes the properties of iron aluminides. This article contains properties such as melting point, electrical resistivity, thermal conductivity, thermal expansion and mechanical properties of various compositions FeAl.

In the publication J. Baker "Flow and Fracture of FeAl", pages 101-115, presented at the TMS Conference in 1994, provides an overview of fluidity and resistance to destruction B2-shape connect the deposits FeAl. This article argues that prior heat treatment strongly affects the mechanical properties of FeAl and high cooling rate after annealing at high temperature leads to the increase of the yield strength at room temperature and strength but reduces ductility due to excessive voids.

In the publication D.J. Alexander "Impact Behavior of FeAl Alloy FA-350", pages 193-202, presented at the TMS Conference in 1994, describes the behavior at impact and tensile zhelezoiridievykh alloy FA-350. This alloy comprises, in atomic %: 35.8% of Al, 0.2% Mo, 0.05% of Zr and 0.13% S.

In the publication S.N. Kong "The Effect of Ternary Additions on the Vacancy Hardening and Defect Structure of FeAl", pages 231-239, presented at the TMS Conference in 1994, described the effect of ternary alloying additives on the FeAl alloys. This article discusses the effects of various ternary alloying additives, such as Cu, Ni, Co, Mn, Cr, V and Ti, and annealing at a high temperature and further processing at a low temperature.

In the publication D.J. Gaydosh "Microstructure and Tensile Properties of Fe40At. Pct. Al Alloys with C, Zr, Hfand In Additions" in September 1989, Met. Trans A, vol. 20A, pp. 1701-1714, described hot pressing powdered gas powder, in which or in powder pre-injected With, Zr and Hf as additives, or add in a pre-prepared Galatasaray powder.

In the publication C.G. mckamey's et al. "A review of recent developments in Fe3Al-based Alloys" in the Aug is the 1991, J. of Mater. Res., Vol. 6, No. 8 p. 1779-1805 described methods of obtaining gentoolinux powders by spraying the inert gas and the production of powders for ternary alloys based on the Fe3Al by mixing powders to obtain the desired alloy composition and compaction by hot pressing, that is, to obtain powders on the basis of Fe3Al spraying with compressed nitrogen or argon and bring to a final density compression molded at 1000°reducing the surface area of ≤9:1.

In U.S. patent No. 4917858, 5269830 and 5455001 described methods of powder metallurgy to obtain intermetallic compositions by: (1) rolling the powder mixture in the unfired tape, sintering and pressing the foil to the final density, (2) chemical reactions during sintering of powders of Fe and Al with the formation of aluminide iron, or the production of composite powders of Ni-B-Al and Ni-B-Ni by chemical spraying, rolling the powder in the tube and heat, cold rolling of powder in the tube and heated to obtain intermetallic compounds. In U.S. patent No. 5484568 described method of powder metallurgy for manufacturing heating elements by microoperations synthesis, in which wave from burning turns the reactants to the desired product. In U.S. patent No. 5489411 described method of powder metallurgy to obtain ti is ANO aluminum foil by plasma spraying on the tape roll, relieve residual stresses by thermal processing, blending the raw surfaces of two such strips and welding them passing through the crimping rolls, and then annealing in solution, cold rolling and intermediate annealing operations.

In U.S. patent No. 3144330 described method of powder metallurgy for manufacturing tapes from electroresistive gentoolinux alloys by hot and cold rolling of elemental powder, pre-mixed powders or their mixtures. In U.S. patent No. 2889224 described method of manufacturing sheets of powdered carbonyl compounds of Nickel or iron by cold rolling of powder and annealing.

Titanium alloys are the subject of numerous patents and publications including U.S. patents№№ 4842819, 4917858, 5232661, 5348702, 5350466, 5370839, 5429796, 5503794, 5634992 and 5746846, Japanese patent publication No. 63-171862, 1-259-139 and 1-42539, European patent publication No. 365174 and articles V.R. Ryabov et al. "Properties of the Intermetallic Compounds of the System Iron-Aluminum, Metal Metalloved, 27, No.4, 668-673, 1969; S.M. Barinov et al. "Deformation and Failure in Titanium Aluminide", Izvestiya Akademii Nauk SSSR are metally, No.3, 164-168, 1984; W. Wunderlich et al. "Enhanced Plasticity by Deformation Twinning of Ti-Al-Base Alloys with Cr and Si", Z. Metallkunde, 802-808, 11/1990; T. Tsujimoto "Research, Development and Prospects of TiAl Intemetallic Compound Alloys", Titanium and Zirconium, Vol. 33, No.3, 19 pages, 7/1985; N. Maeda, "High Temperature Plasticity of Intermetallic Compound TiAl", Material of 53rdMeeting of Superplasticity, 13 pages, 1/30/1990; N. Maeda et al. "Improvement in Ductility of Intermetallic Compound through the Grain uperrefinement", Autumn Symposium of the Japan Institute of Metals, 14 pages, 1989; S. Noda et al. "Mechanical Properties of TiAl Intermetallic Compound", Autumn Symposium of the Japan Institute of Metals, 3 pages, 1988; H.A. Lipsitt "Titanium Aluminides - An Overview", Mat. Res. Soc. Symp. Proc. Vol. 39, 351-364, 1985; P.L. Martin et al. "The Effects of Alloying on the Microstructure and Properties of Ti3Al and TiAl" by ASM in Titanium 80, Vol. 2, 1245-1254, 1980; S.H. Whang et al. "Effect of Rapid Solidification in the L10TiAl Compound Alloys", ASM Symposium Proceedings on Enhanced Properties in Structural Metals Via Rapid Solidification, Materials Week, 7 pages, 1986; and D. Vujic et al. "Effect of Rapid Solidification and Alloying Addition on Lattice Distortion and Atomic Ordering in the L10TiAl Alloys and Their Ternary Alloys", Metallurgical Transactions A, Vol. 19A, 2445-2455, 10/1988.

Methods, kotorii you can handle aluminides TiAl and obtain the required properties described in numerous patents and publications as those indicated above. Furthermore, in U.S. patent No. 5489411 described method of powder metallurgy to obtain a titanium-aluminum foil by plasma spraying on the tape to a roll of residual stresses by thermal processing, blending the raw surfaces of two such strips and welding them passing through the crimping rolls, and then annealing in solution, cold rolling and intermediate annealing operations. In U.S. patent No. 4917858 described method of powder metallurgy for manufacturing titanium-aluminum foil using elemental titanium, aluminum and other alloying elements. In U.S. patent No. 5634992 described processing method γ-titanium aluminide by upl is Tania casting and heating it to a temperature above eutectoid, getting γ-grain plus lamellar colonies αand γ-phase heating to a temperature below eutectoid for growth γ-grains in the structure of colonies and heating to a temperature below the transition in α-phase to convert the remaining structures of the colonies in the structure with α2rails γ-beans.

As seen above, in this area there is a need for an economical method of obtaining metal products, subjected to cold working, such as iron aluminides, Nickel and titanium. Preferably, the compositions of aluminides you could get economical method for the manufacture of these products.

The invention

The invention provides a method of manufacturing subjected to cold working of the products of the compositions of metal alloys, comprising the stage of: (a) upon receipt of the product, which is subjected to hardening by cold working the metal alloy composition to such an extent that it is formed of the surface-hardened zone, (b) heat treatment subjected to hardening of the product by passing it through an oven so that it is subjected to the instantaneous annealing duration less than one minute, and optionally (C) repeating steps (a) and (b) until, until there is obtained a product of the desired size. The metal alloy may be an alloy is elesa type steel, an alloy of copper, aluminum, titanium, zirconium, Nickel or an alloy based on them, or intermetallic composition. The metal alloy is preferably an alloy of iron, Nickel or titanium with aluminum. Instant annealing is preferably carried out using infrared radiation, and cold treatment of the alloy is preferably in the cold rolling of sheets, strips, round and tape profile or wire. In addition, the cold processing of metal alloy may be in the stamping or pressing products of a complex profile.

The method may include casting alloy and hot processing of castings before stage (a). In addition, the alloy can be obtained by powder metallurgy - a film by casting or rolling. For example, the alloy can be obtained by film casting of the alloy powder mixture with a binder, getting loose sheet metal having a porosity of not less than 30%, which is then heated to remove volatile components and process compacted sheet metal, getting the hardened product. In the case of rolling powder alloy mixture with the binder rolled in unconsolidated sheet metal having a porosity of not less than 30%, which is then heated to remove volatile components from unconsolidated sheet metal after cold working receive UE is onenoa product which is subjected to work hardening. The method may include plasma spraying a powder of the alloy on the substrate so as to obtain a non-metallic sheet having a porosity less than 10%, by cold working which receive a hardened product which is subjected to work hardening.

According to a preferred embodiment of the subject cold treatment products get electroresistive heating element that can heat up to 900°With less than 1 second feeding him voltages up to 10 volts and current up to 6 amps. The resistive heating element can be used in various heating devices, such as electric lighters. Electrical resistivity of the resistive heating element is preferably from 80 to 400 μΩ·cm, preferably from 140 to 200 μΩ·see

Intermetallic alloy may be Fe3Al, Fe2Al, Fl3, FeAl, FeAlC, Fe3AlC or their mixture. Intermetallic alloy can be Galatasaray alloy containing ≤32 wt.% Al, ≤2 wt.% Mo, ≤1 wt.% Zr, ≤2 wt.% Si, ≤30 wt.% Ni ≤10 wt.% Cr, ≤0.3 wt.% C ≤0.5 wt.% Y ≤0.1 wt.% In, ≤1 wt.% Nb, ≤3 wt.% W ≤1 wt.% TA. For example, the alloy may contain 20-32 wt.% Al, 0.3 to 0.5 wt.% Mo, 0.05 to 0.3 wt.% Zr, 0.01 to 0.5 wt.% C ≤0.1 wt.% In, 𢙁% oxide particles, the rest is Fe. Preferred Galatasaray alloy contains 20-32 wt.% Al, 0.3 to 0.5 wt.% Mo, 0.05 to 0.3 wt.% Zr, 0.01 to 0.5 wt.% C ≤1% of the particles of Al2About3the rest is Fe.

A short list of drawings, which depict:

Figure 1 - the change in the hardness profile strips FeAl after running rollers.

Figa - influence of heating on the hardness of the sheet of FeAl thickness 8/1000 of an inch.

Fig.2b - effect of duration of heating on the hardness of the sheet of FeAl thickness 8/1000 of an inch when heated to 400°C.

Pigs - effect of duration of heating on the hardness of the sheet of FeAl thickness 8/1000 of an inch when heated to 500°C.

Figure 3 the effect of duration of heating at the temperature at different points of the sheet of FeAl thickness 8/1000 of an inch while passing through the furnace with infrared heat.

Figure 4 - comparison of different rolling processes for sheets obtained by film casting.

Disclosure of the invention

The invention provides a new and economical method of manufacturing subjected to cold treatment products from metallic materials that are subjected to work hardening. The method of the present invention is particularly useful in the manufacture of rolled, stamped or pressed metal alloys of iron type steel, copper alloys, aluminum, titanium, zirconium, Nickel, or alloys and the basis and intermetallic compositions, such as materials from aluminides. Metallic materials can be obtained by casting, powder metallurgy or plasma spraying. In the case of casting the appropriate alloy can be melted, cast from him the harvesting and processing to the final or intermediate profile. In the case of powder metallurgy of elemental powders can be subjected to reactions of chemical synthesis with the formation of the desired composition of the alloy, or can be subjected to spray the appropriate composition of the alloy with the formation of the finished powder, then in both cases, the powder can be subjected to sintering and processing to the final or intermediate profile. In the case of plasma spraying the appropriate composition of the alloy can be melted and sprayed onto the substrate with the formation of the intermediate profile. According to the invention, of the intermediate profile, you can get the profile of the final size in a way that allows you to reduce the number of working operations, such as gangways during rolling.

Usually difficult to handle the composition of metals such as aluminum, especially in the form of thin strips, susceptible strain hardening (work hardening) process. When designing method of the present invention it was found that the strain hardening with the achala occurs in a thin surface layer and gradually increases across the thickness of the material, being cold worked type seal. According to the invention, the initial thin layer, strain-hardened, heat treated, which reduces the hardness of the surface layer. Special benefit is provided to a heat treatment according to the invention is the instantaneous annealing, in which the sheet surface is quickly heated to a temperature sufficient to relieve tension caused in the surface layer. Instant annealing may be conducted in any convenient way, for example by means of infrared, laser, induction heating devices. Especially preferred method of heating in the case of manufacturing sheet material is oven, equipped with infrared lamps arranged so that they would heat the surface of the sheet passing through the oven. The effectiveness of the instantaneous annealing in reducing the hardness of the surface layer will be explained below with reference to one example of the method of obtaining gentoolinux sheets.

Figure 1 shows the hardness profile run-in rollers strips of FeAl before and after stress by annealing. As shown by the markersrepresenting the state of the strip to annealing, it is surface-hardened area in which the indicator of the Vickers hardness is much higher at the surface is t, than in the center. However, as can be seen on markersthe hardness is substantially averaged across the thickness of the strip after removal of the voltage instantaneous annealing in accordance with the invention.

Figa shows how the duration of heating and the temperature influence on the micro-extruded sheet of FeAl thickness 8/1000 of an inch. As shown by the markerscorresponding heat for about 2 seconds, the hardness is reduced to the lowest level at about 400°C. similarly, as shown by the markerscorresponding to the heat within 5 seconds, the hardness is reduced to the lowest level at about 400-500°C. Markerscorresponding heat for 10 seconds, show that the hardness is reduced to the lowest level at about 500°C. As shown by the markerscorresponding heat for 20 seconds, the hardness is reduced to the lowest level at about 500°C. Markerscorresponding to the heat for 30 seconds, show that the hardness is reduced to the lowest level at about 500°C. Consequently, the instantaneous annealing at 400-500°for 2-30 seconds sufficient to reduce strongly the ti surface layer of cold-rolled strips of FeAl.

Fig.2b shows how the duration of the heating effect on the microhardness of a sheet of FeAl thickness 8/1000 of an inch when heated to 400°C. From the graph you can see that after 10 seconds of heating, the hardness is reduced to a level that remains essentially constant and in case of prolonged heating.

Figs shows how the duration of the heating effect on the microhardness of a sheet of FeAl thickness 8/1000 of an inch when heated to 500°C. From the graph you can see that after 10 seconds of heating, the hardness is reduced to the maximum extent and the duration of heating does not cause a further reduction in the hardness of the strip.

Figure 3 shows how the duration of the heat affects the temperature at different points of the sheet of FeAl thickness 8/1000 of an inch while passing through the furnace infrared heater. In this graph markersmeet the top center of the strips, markers correspond to the top of the edge strips and markerscorrespond to the lower center of the strips. Infrared furnace was equipped with an infrared lamps operating at 37% capacity, and the strip was passed through the furnace at a speed of 2 feet per minute. Temperature strips were about 400°With about 35 seconds. By passing through the furnace all three points on the strip is first heated is practically to the same temperature in the first 35 seconds. Then, when the temperature of the strips fell, the upper and lower centers of the strips remained close in temperature, and the top edge was about 50°colder than the Central part.

Figure 4 shows the comparison of different processes for rolling sheets of FeAl thickness 26/1000 inch, obtained by film casting. Here tokenscorrespond to the comparative method, comprising 40 cold rolling passes, and tokensconsistent with the method of the present invention. Comparative method required two intermediate annealing under vacuum (1 hour at 1150°and 1 hour at 1260°and final annealing (1 h at 1100°C), whereas the method of the present invention required only one intermediate annealing under vacuum (1 hour at 1260°and final annealing under vacuum (1 hour at 1100°). However, while the comparative method required 40 passes cold rolling to obtain strips with thickness of 8/1000 of an inch, the method of the present invention, which is instantaneous annealing after each pass of rolling, requiring only 17-18 passes to achieve the same bands. Thus, since the method of the present invention leads to a reduction in the number of cold rolling operations necessary for the manufacture of strips of the desired thickness, this method mn is considerably increases the production efficiency.

In cold rolling gentoolinux alloys in thin strips intermediate annealing operation is best carried out under vacuum in order to minimize oxidation of the bands. The use of such protective atmosphere necessarily entails the use of expensive equipment furnaces and slows down the production process. The present invention makes it possible to increase the speed of production of sheet materials by reducing the number of technological operations and reduce costs by eliminating protective atmosphere on stage instantaneous annealing.

The method according to the invention can be used for various gentoolinux alloys, containing not less than 4 wt.% aluminum and having a different structure depending on the contents of Al: phase Fe3Al has a structure DO3and the FeAl phase has a structure B2. These alloys are preferably ferritic and do not contain astenicheskij microstructures; they may contain one or more alloying elements selected from molybdenum, titanium, carbon, such rare earth elements such as yttrium or cerium, boron, chromium oxide type Al2About3and Y2About3and carbidopazapomnit element (zirconium, niobium and/or tantalum), which can be used together with the carbon for the formation of carbide phases in a matrix of solid races the thief in order to control the grain size and/or dispersion hardening.

The concentration of aluminum in the alloys of the FeAl phase can range from 14 to 32% (nominally), and you can develop such zhelezohromovye alloys, which when processed by pressure or by powder metallurgy methods will possess the required level of ductility at room temperature after annealing in the atmosphere and at a given temperature above 700°With (for example 700-1100° (C) followed by cooling in a furnace, in air or quenching in oil, while maintaining the yield strength, tensile strength, resistance to oxidation and corrosion in the water.

The concentration of the alloying components used in the formation of Fe-Al alloys in the present invention is expressed in nominal weight percent. However, the nominal weight of the aluminum in these alloys is almost equivalent to about 97% of the actual weight of aluminum in them. For example, if the nominal 18,46 wt.% in fact, 18,27 wt.% aluminum, which is about 99% of the nominal concentration.

Fe-Al alloys can be processed or legitamate one or more elements to improve properties such as strength, ductility at room temperature, oxidation resistance, corrosion in the water, pitting corrosion, thermal fatigue, electrical resistivity, resistance to sagging or floor is uchesti at high temperatures and resistance to sickness.

From containing aluminum alloys based on iron can be produced electroresistive heating elements. However, the composition of the alloys of the present invention can also be used for other purposes, such as thermal spraying, in which these alloys may be used as coatings which are resistant to oxidation and corrosion. These alloys can also be used as electrodes, resistant to oxidation and corrosion in furnaces and reactors, the materials resistant to solifidian as corrosion resistant materials for the chemical industry, in pipelines for the transportation of coal slurry or coal tar pitch as the media in the catalytic converters of exhaust gases in the exhaust pipe for automobile engines, porous filters, etc.

According to one aspect of the invention the geometry of the alloy can be varied to optimize the resistance heater according to the formula: R=ρ(L/W×T), where R is the resistance of the heater, ρ is the resistivity of the material of the heater, L - heater length, W - width of the heater and T is the thickness of the heater. The resistivity of the material of the heater can be changed by altering the aluminum content in the alloy processing alloy or introducing alloying additives.

The material for the heater can be manufactured RA is personal ways. For example, it can be produced by casting or powder metallurgy. When the powder metallurgy alloy can be obtained from a pre-prepared powder mixture by mechanical mixing of the component parts of an alloy or a chemical reaction between iron and aluminum powders after this powder mixture was molded product type sheet of cold rolled powder. Mechanically mixed powder can be processed by standard methods of powder metallurgy - conclusions in the form and pressing, slip casting, hot pressing and hot isostatic pressing. Another way is to use powders of pure elements Fe, Al and optional alloying elements. Optionally, you can enter the electrically insulating or electrically conductive particles in the powder mixture, to purposefully change the physical properties and resistance to creep at high temperature material for heaters.

Material for heaters can be manufactured from a powder consisting of various factions, however, preferably such powder mixture consists of particles smaller than 100 mesh. The powder can be obtained by spraying the melt by gas, and the powder can acquire a spherical shape. Alternatively, the powder can get the ay spray in water or polymer, when this powder can acquire a complex shape. Dispersed in the polymer powder contains more carbon and less oxidized from the surface than the powder, dispersed in water. Obtained by spraying in water, the powder may have a film of oxides of aluminum on the surface of particles, and these oxides can rezmelts and to penetrate into material for heaters with thermomechanical processing of powder to obtain such profiles, as sheets, rods, etc. Particles of aluminum oxide, depending on their size, distribution and number can cause an increase of the resistivity zhelezoiridievykh alloy. Moreover, particles of aluminum oxide can be used to increase the strength and resistance to creep, it is not always reduced plasticity.

In order to improve such properties of the alloy, as thermal conductivity and/or resistivity, may insert metal elements and/or particles of electrically conductive or electrically insulating metal compounds. These elements and/or compounds of metals include oxides, nitrides, silicides, borides and carbides of elements selected from groups IVb, Vb and VIb of the Periodic table. They include the carbides of Zr, TA, Ti, Si, etc., borides of Zr, TA, Ti, Mo, etc., silicides Mg, CA, Ti, V, Cr, Mn, Zr, Nb, Mo, TA, W and the like, nitrides of Al, Si, Ti, Zr and the like, oxides of Y, Al, Si, Ti, Zr, etc. In the case when eAl alloy dispersion strengthened oxides, they can be added to the powder mixture, or to obtain in situ by adding pure metal type Y in the molten metal, where Y can be oxidized in the melt, when spraying the melt into a powder and/or during subsequent processing of the powder. For example, the material for heaters can be entered particles of electrically conductive material - nitrides of transition metals (Zr, Ti, Hf), carbides of transition metals, borides of transition metals and MoSi2in order to ensure good resistance to creep at high temperatures up to 1200°s and high resistance to oxidation. In the material for heaters you can also enter the particles of electrically insulating material - Al2O3, Y2About3Si3N4, ZrO2to make the material resistant to creep at high temperatures, as well as to increase its conductivity and/or decrease in the coefficient of thermal expansion.

Upon receipt zhelezoiridievykh alloy casting if necessary, the casting can be cut into pieces of appropriate size, and then to reduce the thickness by rolling or heat treatment at a temperature in the range from 900 to 1100°hot rolling at a temperature in the range from 750 to 1100°C, warm rolling at a temperature in the range from 600 to 700°and/or cold rolling at room themes is the temperature value. With each pass through the mill rolls, the thickness is reduced by 20-30%, followed by instantaneous annealing at 400-500°C.

Cold-rolled product can also be subjected to heating in air, inert gas or vacuum at a temperature in the range from 700 to 1050°With, for example at 800°C for 1 hour. For example, the workpiece can be cut into pieces with a thickness of 0.5 inch (12.7 mm), rolled into a circle at 1000°reducing the thickness of the pieces to 0.25 inch (6.35 mm) (reduced 50%), then subjected to hot rolling at 800°C, reducing the thickness of the pieces to 0.1 inch (2.54 mm) (down 60%)and then subjected to warm rolling at 650°while receiving the sheet thickness 0.030 " (0,762 mm) (down 70%). Then these sheets of thickness 0.030 " (0,762 mm) can be subjected to cold rolling and instant annealing according to the invention.

According to the invention, of the composition of the intermetallic alloy you can get the sheets by forming the finished powder mixture, cold working and annealing of cold rolled sheets. For example, ready powder mix is possible to form a sheet, which can be subjected to cold working (i.e. without the supply of heat from the outside during processing) until you get the desired thickness.

According to this embodiment, the sheets of the composition of the intermetallic alloy produced by powder metallurgy, in which by formula the Oia prepared powder mixture of the composition of the intermetallic alloy is formed unconsolidated sheet metal, which by the compression and reduction of thickness by cold rolling is formed of cold rolled sheet, which is then subjected to heat treatment for sintering, annealing, stress relieving and/or degassing of the sheet. The operation of forming sheet can be carried out in various ways - by the rolling of powder, film casting or plasma spraying. At the stage of molding may be formed from a sheet or thin sheet in the form of strips of any convenient thickness, for example less than 0.1 inch (2.54 mm). Then these strips by cold rolling is brought to the required thickness in one or

several passes along with at least one stage of heat treatment type sintering, annealing or stress relieving. According to the invention, at least one of the operations of heat treatment is instantaneous annealing. This method provides a simple and cost-effective production method to obtain materials from intermetallic alloys type gentoolinux, which are known to have a weak plasticity and highly susceptible strain hardening at room temperature.

In the process of compaction by rolling powdered alloy is subjected to the following processing. Pure elements and alloying additives are preferably dispersed in water or in the polymer so as to form a ready then the shock with particles of complex shape of the intermetallic composition type aluminide (aluminide iron, Nickel or titanium) or other intermetallic composition. Dispersion in water or in the polymer is more preferable than the sputtering gas for subsequent compaction of powder rolling, because the complex shape of the powder particles by spraying in water provides better mechanical grip than spherical particles formed during the sputtering gas. Dispersion in the polymer is more preferable than the dispersion in water, since the dispersion in the polymer powder contains less oxides on the surface of the particles.

The finished powder is sieved, selecting particles of the desired size, is mixed with an organic binder, optionally mixed with a solvent and stirred so as to form a powder mixture. If zhelezoiridievykh powder after sieving particle size should preferably be in the range from -100 to +325 mesh, which corresponds to a particle size of from 43 to 150 μm To improve the fluidity of the powder is not more than 5%, preferably 3-5% of the powder particles should have a size smaller than 43 μm

Semi-bands obtained by rolling a powder in which the powder mixture is fed from the hopper through a slot in the cavity between the two crimping rollers. In the preferred embodiment by rolling the powder is prefabricated gentoolinux strips thickness was 0.026 inch (0.66 mm)to the th can be cut into strips the size of 36 inches by 4 inches (of 91.44 cm 10,44 cm). Semi-finished products subjected to heat treatment to remove volatile components such as the binder and any organic solvents. The burning out of the binder can be carried out in a furnace at atmospheric or reduced pressure in a continuous or periodic mode. For example, the party gentoolinux strips can be loaded into the furnace at an appropriate temperature, for example 700-900°F (371-482° (C)that the relevant period of time, for example 6 to 8 hours, at elevated temperature, for example, 950°F (510°C). During this operation, the furnace can be blown with nitrogen at a pressure of 1 ATM in order to remove most of the binder, at least 99%. Such removal of the binder leads to greater fragility of semi-finished products, which are then subjected to primary sintering in a vacuum furnace.

During the primary sintering porous, fragile stripes, devoid of binder, is subjected to heat, preferably under conditions that cause partial sintering of powder or seal or no seal. This sintering can be carried out in an oven under reduced pressure, in a continuous or periodic mode. For example, the party deprived of the binder gentoolinux strips can be heated in a vacuum furnace at an appropriate temperature, for example 2300°F (1260° (C)within the applicable time, for example 1 hour. Vacuum furnace can in order to keep any convenient vacuum pressure, for example, from 10-4up to 10-5Torr. To prevent loss of aluminum from strips during sintering preferably the temperature should be maintained at a sufficiently low level so as to avoid evaporation of aluminum, but to provide sufficient strength for subsequent rolling. In addition, the sintering is preferably carried out under vacuum to avoid oxidation of unconsolidated bands. However, instead of vacuum, you can use the protective atmosphere of the type of hydrogen, argon and/or nitrogen with the proper dew point of -50°F or less.

The next phase sintered strip is preferably subjected to cold rolling on the air until the final or intermediate thickness. At this stage, the porosity of the semi-finished product can be significantly reduced, for example from 50% to less than 10%. Due to the hardness of the intermetallic alloy is best to use a 4-high rolling mill in which the rollers in contact with the strip of intermetallic alloy, preferably have a carbide surface. However, you can apply commercials of any convenient construction, for example rolls of stainless steel. Moreover, when applying the instantaneous annealing in accordance with the invention eliminates the need to use carbide rollers during cold rolling. If you use steel rollers, predpochtite the flax should limit the degree of compression with the to the rolled material is not deformed rollers due to the hard-working intermetallic alloy. Cold rolling is preferably carried out so as to reduce the thickness of the strips not less than 30%, preferably not less than 50%. For example, sintered zhelezohromovye strip thickness was 0.026 inch (0.66 mm) can roll out to a thickness of 0.013 inch (0.33 mm) in a single stage cold rolling in one or more passes.

After each operation of the cold-rolled strip is subjected to heat treatment for annealing. The annealing may be the primary annealing in a vacuum furnace in periodic mode or in a furnace filled with such gases as H2N2and/or Ar, in continuous mode and at a temperature suitable for stress relieving and/or further compaction of the powder. In the case of aluminide iron primary annealing may be conducted at any suitable temperature, for example 1652-2372°F (900-1300°C), preferably 1742-2102°F (950-1150°C) for one or more hours in a vacuum furnace. For example, cold-rolled strip from aluminide iron can be annealed for 1 hour at 2012°F (1100°C), however, the surface quality of the sheet can be improved in the same or another operation heating by annealing at a higher temperature, for example 2300°F (1260°C)for 1 hour. Periclytos may be accompanied by or be replaced by a stage instantaneous annealing, as described previously.

After a stage of annealing, the strip may not necessarily be brought to the desired size. For example, the strip can be cut in half and subjected to additional operations of cold rolling and heat treatment.

The next phase of the band after the initial rolling subjected to further cold rolling to reduce their thickness. For example, zhelezohromovye strip can roll 4-roll rolling mill so that their thickness decreases from 0.013 to 0.010 inch (0.33 mm to 0,254 mm). At this stage the degree of compression of not less than 15%, preferably about 25%. Every stage of a rolling should preferably stage instantaneous annealing, as described previously. However, if desired, one or more stages of annealing can be skipped, for example, strips of a thickness of 0.024 inch (0.6 mm) you can roll out at primary cold rolling up to 0.010 inch (0,254 mm). Subsequently the band after the second cold rolling can optionally be subjected to secondary sintering and annealing. When the secondary sintering and annealing of the strip can be heated in a vacuum furnace in periodic mode or in a furnace filled with such gases as H2N2and/or Ar, in continuous mode for a complete seal. For example, the party gentoolinux strips can be heated in a vacuum furnace at a temperature of 2300°F (1260° (C) is within 1 hour.

After the secondary sintering and annealing of the strip can optionally be subjected to secondary cutting ends and edges as necessary, as in the case of cracking of the edges. Then the strip can be subjected to a third and final cold rolling with intermediate instant annealing. The thickness of the strips is reduced by 15% or more. Preferably the strip is rolled to the final thickness, for example, from 0,010 0,008 inch (0,254 mm to 0.2 mm). After the third or last of the cold-rolled strip can be subjected to final annealing in continuous or batch mode, at temperatures above the recrystallization temperature. For example, when the final annealing party gentoolinux strips can be heated in a furnace at an appropriate temperature, for example 2012°F (1100°C)for 1 hour. When the final annealing the cold rolled sheet is preferably subjected to recrystallization to the desired average grain size, for example from 10 to 30 μm, preferably about 20 μm After this band may not necessarily be the final pruning, in which the cut ends and edges, and the sheet is cut into narrower strips.

Cut strips can be subjected to heat treatment for stress relieving, to eliminate thermal voids formed on PressTV who in later stages of processing. Stress relief by heat treatment increases the plasticity of the material strips (for example, the ductility at room temperature may be increased from 1% to 3-4%). When this heat treatment batch of strips can be heated in a furnace at atmospheric pressure or in a vacuum furnace. For example, zhelezohromovye strip can be heated approximately at 1292°F (700° (C) within 2 hours and slowly cooled in the furnace (with speed ≤2-5°F/min) to the appropriate temperature, for example 662°F (350°C), and then tempering. When removing stresses by annealing temperature of the material gentoolinux strips should preferably be maintained within such limits, when aluminide iron is in the ordered B2 phase.

After removing the stress from strips can be made of tubular heating elements by any convenient method. For example, they can be subjected to laser cutting, mechanical stamping or chemical phototravel to obtain the desired shape of the individual blades. For example, when cutting, you can make some spillovers blades extending from a rectangular base, which after moulding of the pipe and the connection of the seam to form a tubular heating element with a cylindrical base and next along the axis and spaced around the circumference of the heating blades. On the other sides of the, of the uncut strip can be molded blank pipe, and the desired shape cut out of it to get the heating element to the desired configuration.

In order to avoid fluctuations in the quality of cold-rolled sheet, it is desirable to control the porosity, the distribution of the oxide particles, the grain size and surface finish. The oxide particles are formed of the oxide film on the powder, obtained by dispersion in water. They split up and distributed across the sheet during cold rolling. Inhomogeneous distribution of oxides can lead to variations in the properties of one sample or between different samples. The flatness of the surface can be adjusted by controlling the tension when rolling. In General, cold-rolled materials at room temperature exhibit a yield strength in the 55-70 ksi, a tensile strength 65-75 ksi, total elongation at 1-6%, the reduction in the area of 7-12% and electrical resistivity of the order of 150-160 μΩ·cm, whereas when the temperature is raised to 750°they exhibit a yield strength in 36-43 ksi, a tensile strength 42-49 ksi, full extension on 22-48% and a reduction in the area on 26-41%.

According to the method of film casting sheet is formed from the prepared powder mixture. While for rolling preferred powders powders obtained by dispersion in water or in the polymer laplanche preferred casting powders, obtained by spraying the gas, due to the spherical shape of the particles and low oxide content. Sprayed powders in water sift, as in the method of rolling a powder, and sieved powder is mixed with organic binder and solvent so as to form a dense suspension (slurry), from which thin cast sheet, which is treated with cold rolling and annealed as described in the embodiment according to the method of rolling powders.

By the method of plasma spraying non-metallic sheet is formed from the prepared powder mixture by spraying powder of the intermetallic alloy on a substrate. Sprayed droplets are deposited and solidify on the substrate in the form of a flat sheet, which is cooled by the refrigerant on the reverse side. The spraying can be carried out in vacuum, in an inert atmosphere or in air. The thickness of the sheets can be varied during the deposition, and because it can come close to the final thickness of the sheets, the method of thermal spraying has the advantage over conventional rolling of powders and film casting that to obtain sheets requires less stages of cold rolling and annealing.

In a preferred method, a plasma spraying according to the invention, the band width of, for example 4 or 8 inch (101,6 mm or 203.2 mm) is obtained by applying the prepared powder mixture, the scientists in the sputtering gas, in the water or in the polymer on a substrate using a plasma torch, performing forward-backward movement perpendicular to the direction of movement of the substrate. You can get strips of any thickness up to 0.1 inch (2.54 mm). During plasma spraying, the powder is sprayed so that the particles melt when they get on a substrate. The result is a very dense (over 95%) film with a smooth surface. To minimize oxidation of the molten particles, it is possible to make the protective shell and fill it with a protective atmosphere type argon or nitrogen around the plasma jet. However, if the plasma spraying process is carried out in air, it can form a film of oxide on the molten droplets, which will lead to the introduction of oxide in the deposited film. The substrate preferably consists of stainless steel, whose surface is treated by shot blasting to provide a mechanical grip to hold the strips in the deposition process, but could make the strip for further processing. According to a preferred embodiment, zhelezohromovye strips sprayed to a thickness of 0.020 inch (0.5 mm), after which they can be subjected to cold rolling in several passes to 0.010 inch (0.25 mm) intermediate instant annealing, finish cold rolling to 0.008 inch (0.2 mm) and p is durgnat final annealing and heat treatment for stress relieving.

In General, the method of thermal spraying gives a thicker sheet than film casting or rolling of powder. Method of thermal spraying plasma spraying it allows the use of powders, obtained by dispersion of a gas in water or in the polymer, whereas spherical powders obtained by spray gas, not so well compacted in the process of rolling, as powders, dispersed in water. Compared with a film casting thermal spraying gives less residual carbon, because when thermal spraying is not necessary in the application of the binder or solvent. On the other hand, thermal spraying susceptible to contamination by oxides. In a similar way and rolling of powder exposed to pollution by oxides, when used powders, dispersed in water, because after being in the water on their surface could be formed film of oxides, whereas the powders obtained by spray gas, can be almost or completely not contain oxides on the surface.

In the foregoing described the principles, preferred embodiments and modes of application of the present invention. However, this should not be understood in the sense of limiting the invention to these specific embodiments. The above-described embodiment should be considered as given for illustration and not for limitation, and need under the TB, the experts in this field can deviate from these embodiments without going beyond the scope of the present invention, as defined by the following claims.

1. The method of manufacture of the product subjected to cold working, including the production of products, cold treatment followed by rapid annealing, characterized in that the product is made from a metal alloy selected from the group comprising iron aluminides, Nickel and titanium, when cold worked product is subjected to hardening with the formation of surface-hardened areas, and rapid annealing is carried out with a delay less than one minute, and if necessary the operation of the cold processing and rapid annealing repeat until you get the desired dimensions.

2. The method according to claim 1, characterized in that the product is made from aluminide iron.

3. The method according to claim 1, characterized in that the product is made from an alloy containing aluminide iron, in the following ratio, wt.%:

aluminum 4,0-32,0;

chrome ≤1;

iron rest.

4. The method according to claim 1, characterized in that the product is made from aluminide titanium.

5. The method according to claim 1, characterized in that the cold treatment is carried out by cold rolling products, representing sheet, strip, round or tape profile or Provo is the eye.

6. The method according to claim 1, characterized in that the cold treatment is carried out by pressing or stamping products, which are subjected to hardening, to produce the final or intermediate form.

7. The method according to claim 1, characterized in that the product is made from a metal alloy selected from the group comprising Fe2Al, Fe2Al5, FeAl3, FeAlC, Fe3l or mixtures thereof.

8. The method according to claim 1, wherein the rapid annealing is carried out by heating subjected to hardening of the product to a temperature of at least 400°With a time less than 45 C.

9. The method according to claim 1, wherein the rapid annealing is performed in air environment.

10. The method according to claim 1, characterized in that the product is subjected to hardening by cold working, is produced by casting metal alloy and hot-working the cast.

11. The method according to claim 1, characterized in that the product being cold worked, annealed at a temperature of 1100-1300°C in vacuum or inert environment.

12. The method according to claim 1, characterized in that the product is made from an alloy containing aluminide iron, in the following ratio of components in the metal alloy, wt.%:

aluminum ≤32;

molybdenum ≤2;

zirconium ≤1;

silicon ≤2;

Nickel ≤30;

chrome ≤10;

carbon ≤0,3;

Bor ≤0,1;

niobium ≤1;

Wolfram ≤3;

tantalum ≤1;

iron rest.

13. The method according to claim 1, characterized in that the product is made from an alloy containing aluminide iron, in the following ratio of components in the metal alloy, wt.%:

aluminum 20-32;

molybdenum 0.3 to 0.5;

zirconium 0,05-0,3;

carbon 0,01-0,5;

Bor ≤0,1;

oxide particles ≤1;

iron rest.

14. The method according to claim 1, characterized in that the product is made from an alloy containing aluminide iron, the hardness of the surface-hardened zone can reduce not less than 10% by conducting rapid annealing.

15. The method according to claim 1, characterized in that the product is made in the form of a sheet obtained without hot working metal alloy.

16. The method of manufacture of the product subjected to cold working, including the production of products, cold treatment followed by rapid annealing, characterized in that the product is produced by film casting powder mixture of metal alloy and a binder with the formation of loose sheet with a porosity of at least 30%, by cold working, the product is subjected to hardening with the formation of surface-hardened areas, and rapid annealing is carried out with a delay less than one mi is by Uta, moreover, if necessary, the operation of the cold processing and rapid annealing repeat until you get the desired dimensions.

17. The method according to item 16, characterized in that before the cold treatment is carried out by heating unconsolidated sheet to a temperature sufficient to remove volatile components of the binder.

18. The method of manufacture of the product subjected to cold working, including the production of products, cold treatment followed by rapid annealing, characterized in that the product is made by rolling a powder mixture of metal alloy and a binder to form a sheet with a porosity of at least 30%, by cold working, the product is subjected to hardening with the formation of surface-hardened areas, and rapid annealing is carried out with a delay less than one minute, and if necessary the operation of the cold processing and rapid annealing repeat until you get the desired dimensions.

19. The method according to p, characterized in that before the cold treatment is carried out by heating unconsolidated sheet to a temperature sufficient to remove volatile components of the binder.

20. The method of manufacture of the product subjected to cold working, including the production of products, cold treatment followed by rapid annealing, characterized in that the product is produced plasma NAPA is the group of metal alloy with the formation of loose sheet with a porosity of at least 10%, when cold worked product is subjected to hardening with the formation of surface-hardened areas, and rapid annealing is carried out with a delay less than one minute, and if necessary the operation of the cold processing and rapid annealing repeat until you get the desired dimensions.

21. The method of manufacture of the product subjected to cold working, including the production of products, cold treatment followed by rapid annealing, characterized in that the product is made from a metal alloy, cold worked product is subjected to hardening with the formation of surface-hardened zone, rapid annealing is carried out using infrared radiation with exposure less than one minute, and if necessary the operation of the cold processing and rapid annealing repeat until you get the desired dimensions.

22. The method of manufacture of the product subjected to cold working, including the production of products, cold treatment followed by rapid annealing, characterized in that the product is made from a metal alloy selected from the group comprising iron aluminides, Nickel and titanium, when cold worked product is subjected to hardening with the formation of surface-hardened zone, rapid annealing is carried out with a delay less than one minute, and if necessary the operation of the cold processing is fast annealing repeat until you get the desired dimensions, while the product form in the form electroresistive heating element that can heat up to 900°With less than a second feeding him voltages up to 10 volts and currents up to 6 A.

23. The method of manufacture of the product subjected to cold working, including the production of products, cold treatment followed by rapid annealing, characterized in that the product is made of metal alloy in the form of cold-rolled sheet, cold treatment is carried out by cold rolling, subjecting the product to hardening with the formation of surface-hardened areas, with the porosity of the sheet is reduced with more than 50% to less than 10%, and rapid annealing is carried out with a delay less than one minute, and if necessary the operation of the cold processing and rapid annealing repeat until you get the desired dimensions.

24. The method of manufacture of the product subjected to cold working, including the production of products without hot working, cold treatment followed by rapid annealing, characterized in that the product is made from a metal alloy, cold worked product is subjected to hardening with the formation of surface-hardened areas, and rapid annealing is carried out with a delay less than one minute, and if necessary the operation of the cold processing and rapid annealing repeat until you get the desired R is Smurov products followed by a final cold working and subsequent recrystallization annealing.

25. The method of manufacture of the product subjected to cold working, including the production of products, cold treatment followed by rapid annealing, characterized in that the product is made from a metal alloy selected from the group comprising iron aluminides, Nickel and titanium, cold spraying is carried out using rollers with carbide or not carbide surface contact directly with the product, which is subjected to hardening with the formation of surface-hardened areas, and rapid annealing is carried out with a delay less than one minute, and if necessary the operation of the cold processing and rapid annealing repeat until you get the desired dimensions.

26. The method of manufacture of the product subjected to cold working, including the production of products, cold treatment followed by rapid annealing, characterized in that the product is made from a metal alloy selected from the group comprising iron aluminides, Nickel and titanium, when cold worked product is subjected to hardening with the formation of surface-hardened areas, and rapid annealing is carried out with a delay less than one minute, and if necessary the operation of the cold processing and rapid annealing repeat the Ute to get the desired dimensions, while the product form in the form electroresistive heating element with electrical resistivity of 80 to 400 μΩ·see



 

Same patents:

FIELD: mechanical engineering; piston internal combustion engines.

SUBSTANCE: invention relates to valve of internal combustion engine, method of its manufacture and heat-resistant titanium alloy used for manufacture of valve consisting of following components, mass %: aluminum 7.5-12.5; molybdenum 1.6-2.6; zirconium 1.4-2.4; silicon 0.1-0.2' yttrium 0.005-0.1; titanium - the rest. It has α+α2+β phase composition with intermetallide α2 phase on Ti3Al base dispersed in α phase. Proposed method includes forming of valve from cylindrical blank by deformation machining with preliminary heating and subsequent heat treatment. Preliminary heating of part of blank related to rod done to temperature 5-20oC lower than temperature of complete polymorphic transformation of alloy, and its deformation machining is carrying out by wedge cross rolling. Deformation machining of part of blank related to head is done by forging with preliminary heating to temperature 5-50oC higher than temperature of complete polymorphic transformation of alloy corresponding to beginning of forging, and forging is finished at temperature lower than complete polymorphic transformation of alloy to form plate head of valve and transition section provided smooth changing of head into rod. Invention provides designing of valve, method of its manufacture and heat-resistant alloy used in manufacture of valve making it possible to operate valve within operating temperature range owing to increased long-term strength and creep resistant of valve head material and increased strength, modulus of elasticity and hardness of valve rod material.

EFFECT: improved quality of valve and increased reliability in operation.

16 cl, 3 tbl, 1 ex, 15 dwg

-titanium alloys" target="_blank">

The invention relates to ferrous metallurgy, in particular to the processing of titanium alloys

The invention relates to a pressure treatment of metals to improve the physico-mechanical properties, in particular in the manufacture of semi-finished titanium or other metals

The invention relates to the processing of metals by pressure, and in particular to methods of manufacturing fasteners with heads, for example, titanium alloys, and can be used in mechanical and aeronautical engineering
The invention relates to deformation-heat treatment of materials and can be used in mechanical engineering, aircraft engine industry and medicine in the manufacture of semi-finished titanium

The invention relates to the field of metallurgy, in particular to a method of thermo-mechanical processing pipe profile of binary zirconium-niobium alloys, intended for subsequent cold rolling products that are used as structural elements of the active zones of nuclear reactors

The invention relates to mechanical engineering and can be used to improve the fatigue characteristics of parts from titanium alloys, in particular of compressor blades of GTE made of wrought titanium alloys

The invention relates to the field of metallurgy, mainly to processing of metals by pressure, in particular, to methods for producing a sheet of semi-finished products from titanium alloys with a uniform submicrocrystalline structure with grain size less than 1 micron

The invention relates to the field of metallurgy, mainly to processing of metals by pressure, in particular to the technology of production of high strength thin sheets, strip and foil of technical titanium, and can be used in instrumentation, aerospace, and medicine

The invention relates to the processing of metals by pressure, in particular to the preparation of material for further processing methods of forming processes

The invention relates to the field of metal forming, and in particular to a method of hardening mainly plate blanks

The invention relates to mechanical engineering and can be used to harden the finished products of alloy steels, alloys and non-ferrous metals

The invention relates to the processing of materials and products from them, namely, devices hardening metal by methods of surface plastic deformation

The invention relates to the field of shot peening holes in parts and can be used in critical components of turbine engines, parts, units, working in atomic mode, such as on submarines, nuclear power plants, space objects, etc

The invention relates to ferrous metallurgy, in particular to the production of soft magnetic iron

The invention relates to the field of metallurgy, in particular to methods of radiation modification of products from carbidosteel

The invention relates to powder metallurgy, in particular to the manufacture of products with high mechanical properties and high resistance to wear

The invention relates to the field of powder metallurgy

The invention relates to powder metallurgy, in particular to methods for geometrically-complex sintered products, and can be used for the manufacture of the working bodies of submersible centrifugal pumps
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