RU2487174C2 - Method to process iron-carbon melt and material for its realisation - Google Patents

Abstract

FIELD: metallurgy.

SUBSTANCE: method is carried out by foaming of a material introduced into the melt for its processing inside the melt volume. The material contains a calcium-containing substance in the form of a mixture of calcium melt with silicon: and calcium in the metal phase, and also fusible flux from haloids in alkaline and/or alkali-earth metals, carbonates of alkali and/or alkali-earth metals at the following ratio of components, wt %: fusible flux 5-50, carbonates 5-20, calcium-containing substance - balance.

EFFECT: increased temperature-time interval of material and melt reacton, higher efficiency of melt and material reaction.

21 cl, 3 tbl

Description

The invention relates to the field of metallurgy, in particular to out-of-furnace treatment of iron-carbon melts.

There are a significant number of scientific works and monographs on the features of the crystallization processes of modified metals, as well as an analysis of the proposed compositions of the materials used to process the iron-carbon melt. There are also various methods of introducing materials into the melt (in the form of briquettes, blowing powders, return to the stream, etc.), but the most modern and technologically advanced is the method of introducing the material in the form of a filler of flux-cored wire fed into the ladle with a tribamer. At the same time, the pyroeffect and dust emission are significantly reduced, the material consumption is reduced, their absorption by the melt and the processing efficiency are significantly increased. However, most of the known materials for processing iron-carbon melt, including those that are fillers of cored wire, have common disadvantages.

Firstly, it is their low survivability. So, the alkaline earth metals (hereinafter referred to as alkaline earth metals) that are part of the material are characterized by high vapor pressure, low boiling points and, being practically insoluble in the iron melt, they very quickly evaporate and evaporate from the melt, only partially refining and modifying it. At subsequent technological stages - during cooling of the melt and, especially, during its crystallization, when the state of aggregation changes, the refining components of the material are practically absent and new inclusions and segregation are distinguished in the metal. They pollute the boundaries of the formed grains and enhance the segregation manifestations in the metal.

Another disadvantage of the known materials for processing iron-carbon melt is associated with the underdevelopment of their reaction surfaces in the interaction with liquid metal. The sorption capacity of the material, the intensity of the processes of nucleation and binding of phases and inclusions are catalyzed by the “slag-metal”, “gas bubble (alkali-metal vapor) – metal” interfaces and depends on the size of the interface, as well as the surface tension energy of the boundaries.

In traditional, well-known modifiers, when the bubbles of vapor generated in the melt come into contact with the metal only by their surface layers, their refining efficiency is insufficient. Approximately, only 5-10% of the input active substance of the material carries out its refining functions. The main part in the form of unreacted gas (steam) is removed from the metal. Thus, it is necessary to increase the efficiency and duration of the refining and modifying action of the material for processing the iron-carbon melt. Certain actions in this direction are being taken.

As a material for processing an iron-carbon melt, one can indicate, for example, material known according to the patent of the Russian Federation No. 2023044 (class C22C 35/00, application. September 10, 1992, publ. November 15, 1994, “Briquette for deoxidation and modification of steel and cast iron” ) The briquette material includes a barium-containing material (as a barium-containing material it contains Witeritstrontianite concentrate calcined at 1200-1250 K), aluminum powder, fluorspar and 65% ferrosilicon powder in the following ratio, wt.%: Firing product of Witeritstrontianite concentrate 53- 55, aluminum powder 7-12, powder 65% ferrosilicon 29-32, fluorspar 2-3 and binders (low-melting oxides, etc.) 2-4.

The disadvantages of this material include:

- the need for preliminary long-term high-temperature (at 1250K) annealing of the concentrate;

- the presence in the concentrate after annealing of undesirable impurity compounds -Al ₂ O ₃ , SiO ₂ and sulfides;

- low efficiency of such a material in industrial use, associated with its use in the form of briquettes, easily oxidized and burn mainly in slag.

Also known is a material for treating an iron-carbon melt (see RF patent No. 2216603, class C22C 35/00, application form 17.04.2001, publ. November 20, 2003, “Modifier for steel”), in which a material containing, by weight .%:

a powder of ligatures with rare-earth metals (hereinafter REM) 10-40, a powder of ligatures with SHZM 50-80 and a powder of calcium fluoride and / or cryolite 5-10. The particle size of these components: 0.1-1.5 mm; 0.1-3 mm and 0.01-0.1 mm, respectively.

The disadvantages of the material include:

- high REM content, increasing the cost of the modifier;

- slow surfacing in the melt of fairly heavy (4-6 g / cm ² ) inclusions with rare-earth metals and their contamination of the steel structure;

- the danger of developing cerium heterogeneity;

- low efficiency of the use of components of the modifier due to the undeveloped interfacial surface "modifier-melt".

The closest in technical essence, the achieved result and selected as a prototype for the material used to implement the method, is a composition that serves as a filler cored wire containing calcium and silicon. The amount of calcium in the filler is 36-56 wt.%, The ratio between calcium and silicon is in the range (0.6-1.3) :, and the ratio between the calcium content in the filler and the content of the filler in the wire is 0.7-1, 2. In this case, the calcium in the filler is in the form of an alloy with silicon or partially in the metal phase (in the amount of 10-50%), and the ratio between the filler and the steel shell is established as follows, wt.%: 45-61 and 39-55, respectively (see RF patent No. 2234541, according to class C21C 7/00, filed May 23, 2003, published August 20, 2004, “Wire for out-of-furnace treatment of metallurgical melts”).

The disadvantage of this material is the low efficiency of the interaction of the melt with calcium, since the latter, being in the form of a CaSi ₂ phase or calcium metal, has low boiling points (1487 ° С) and melting points (980 ° С), and therefore, high vapor pressure of calcium at temperatures processing of steel melts. As a result, calcium in the composition of such a filler is subject to great waste, has a fairly short temperature-time interval in the melt. In addition, the small total reaction surface of the gas bubble-metal interface does not provide intensive refining and modification.

When developing the composition of the material for treating iron-carbon melt, the task was to increase the quality of steel while reducing the consumption of material for refining and modifying the processing of iron-carbon melt.

The technical result obtained by the implementation of this invention is to expand the temperature-time interval of the interaction of the material with the melt, as well as increasing the efficiency of the interaction of the melt with the material.

This problem is solved due to the fact that the material for processing the iron-carbon melt, including a calcium-containing substance in the form of a mixture of calcium in the metal phase and an alloy of calcium with silicon, according to the invention, additionally contains a low-melting flux of alkali and / or alkaline earth metal halides, alkali and / or carbonates or alkaline earth metals, in the following ratio of components, wt.%:

fusible flux 5-50 carbonates 5-20 calcium substance rest.

In this case, the calcium-containing substance in the form of an alloy of calcium with silicon and / or calcium in the metal phase within its content in the material can be partially replaced by silicobarium and / or aluminum barium in the amount of 3-30 wt.%; the composition of the fusible flux within its content in the material may additionally include AlCl ₃ and / or Na ₃ AlF ₆ in the amount of 3-10 wt.%; and carbonates within their content in the material can be partially replaced by calcium oxide in an amount of 2-15 wt.% and / or a concentrate of barium strontium carbonate in an amount of 5-30 wt.% of the amount of carbonates. In addition, the material for processing the iron-carbon melt may additionally contain carbon in an amount of 0.25-0.35 fractions of the proportion of carbon dioxide in carbonates.

The material for processing the iron-carbon composition can be used as a filler of cored wire, and the low-melting flux can be a flux of eutectic composition.

There is a method of treating an iron-carbon melt by blowing through an inert gas melt (see p. RF No. 214564, class C21C 7/00, application form. 08.20.1998, publ. 02.20.2000 "Method of out-of-furnace steel processing"). The method includes guidance of highly basic slag, deoxidation of steel with aluminum, purging of the melt with argon, metal treatment with calcium-containing materials in the form of a flux-cored wire. In this case, the input of the wire is carried out in 2 stages. The amount of introduced calcium-containing materials in terms of the calcium absorbed by the metal is set at the first stage depending on the amount of sulfur removed from the metal, and at the second, depending on the content of residual aluminum. As calcium-containing material, it is possible to use silicocalcium.

The disadvantages of this analogue are the low efficiency of the use of the modifier, due to its consumption for desulfurization, and the associated high cost of modification, as well as the use of a modifier having low “survivability” in the iron melt, argon purge facilitates the removal of which from the melt.

The closest in technical essence, the achieved result and selected as a prototype is a method of processing an iron-carbon melt by introducing into the melt material for its processing, forming discrete gas bubbles in the melt (see cl. RF No. 2234541, according to class C21C 7/00, Declared May 23, 2003, published August 20, 2004, “Wire for out-of-furnace treatment of metallurgical melts”). The method includes introducing into the melt the material for processing it in the form of a flux-cored wire containing calcium and silicon. In the filler of cored wire, the amount of calcium is 36-56 wt.%, The ratio between calcium and silicon is in the range (0.6-1.3): 1, and the ratio between the content of calcium in the filler and the content of the filler in the wire is 0.7 -1.2. In this case, the calcium in the filler is in the form of an alloy with silicon or partially in the metal phase (in the amount of 10-50%), and the ratio between the filler and the steel shell is established as follows, wt.%: 45-61 and 39-55, respectively.

The disadvantage of this method is the low efficiency of the interaction of the melt with calcium, since the latter, being in the form of a CaSi ₂ phase or calcium metal, has low boiling points (1487 ° С) and melting points (980 ° С), and therefore, high vapor pressure of calcium at temperatures processing of steel melts. As a result, calcium in the composition of such a filler is subject to great waste. He, forming separate discrete bubbles, quickly floats to the surface of the melt, having a fairly short temperature-time interval of being in the melt. In addition, the small total reaction surface of the gas bubble-metal interface does not provide intensive refining and modification.

When developing a method for processing iron-carbon melt, the task was to improve the quality of steel while reducing the consumption of material for refining and modifying processing of iron-carbon melt.

The technical result obtained by the implementation of this invention is to increase the temperature-time interval of the interaction of the material with the melt, as well as increasing the efficiency of the interaction of the melt with the material.

The problem is solved due to the fact that in the known method for processing an iron-carbon melt by introducing material into the melt for processing it, according to the invention, the melt is processed by foaming the material of claims 1-19 within the melt volume.

The foaming of the material according to claims 1 to 19 of the claims within the melt volume can be carried out by carbon dioxide, which is formed during the decomposition of the material introduced into the melt in the volume of 8-40 ncm ³ / g of material.

Studies conducted on the sources of patent and scientific and technical information have shown that the claimed method and material are unknown and do not follow explicitly from the studied prior art, i.e. meet the criteria of novelty and inventive step.

The inventive material can be obtained, and the inventive method and material can be used at any enterprise specializing in this industry, because this requires well-known components and standard equipment, i.e. they are industrially applicable.

The theoretical justification of the proposed solution is based on the boundary-catalytic refining processes and is as follows:

1. The development of thermally activated processes of nucleation, development and transformation of phases proceeds the easier, the more developed is the “melt-melt” interface and the lower is the surface tension of their boundaries. Surface active elements, primarily alkaline earth and alkali metals, are practically insoluble in iron melts, but they segregate and enrich the boundaries, reducing their energy. Therefore, both the release rate and the ability to adsorb increase in proportion to the increase in the length of the boundaries. In this case, the “melt - gas-flux-bubble interface” interface. The phases, precipitates, and impurities that arise and adhere to such boundaries are ultimately carried out by the flotation mechanism with bubbles to the surfaces and are assimilated in the slag. Such a bubble-foamed structure of an emulsified dispersion system leads to maximum effective deoxidation, refining and modification of non-metallic inclusions. In contrast, the flotation effect of bubbles blown through the melt of an inert gas occurs discretely and therefore the above processes proceed less efficiently.

2. The efficiency of foaming of the filler material mainly occurs at the exit of the molten modifier from the reaction space of the cored wire sheath into the steel-ladle metal. Those. when a flux-cored wire is introduced into the metal even before the steel sheath melts, the filler located in the lower part of the steel ladle should be mainly liquid. However, not all its constituent components have sufficiently low melting points. So, silicocalcium, fluorides melt at temperatures exceeding 1000-1100 ° C. Therefore, the presence of components that melt at sufficiently low temperatures, and they can be alloys of at least two halides, with a ratio of their concentrations close to eutectic, is required. As an example, Table 1 shows the melting points of a number of alkaline and alkaline-earth halides and their concentration at eutectic compositions. These data illustrate the possibility of a significant (by hundreds of degrees Celsius) decrease in the melting temperature of mixtures at their contents close to eutectic ratios.

Table 1 Eutectic compositions and melting temperatures of alloys of salts of alkali and alkaline earth metals. Structure T _EVT , ° C 30-40% NaCl + 60-70% Na ₂ COa 638 50% NaCl + 50% BaCl ₂ 648 40% NaF + 60% Na ₂ CO ₃ 660 70-75% NaCl + 25-30% NaF 675 80% CaCl ₂ + 20% CaF ₂ 650 40% NaCl + 60% MgCl ₂ 450 70 mol. % NaF + 30 mol. % CaF ₂ 810

25% NaCl + 75% CaCl ₂ 500 40% NaCl + 60% KCl 650 60% KF + 40% NaF 698 50% KCl + 50% NaCl 658 70% NaCl + 30% NaF 674 30% CaO + 70% CaF ₂ 1550

It has been established that in such a melt high-temperature compounds capable of dissolving in the substitution, exchange, etc. reaction with the ingredients of the melt are capable of dissolving. Thus, higher-temperature components capable of dissolution pass into the low-temperature melt. Moreover, as a result of chemical interactions of various types, complex compounds can change valency and recover to metal, salt fluxes become more inhomogeneous, viscous and boil in a sufficiently wide temperature range, extend the temperature-time interval of interaction with the melt, participating in active refining of the melt up to temperatures its crystallization.

Due to their high adhesion properties, such fluxes easily foam, in particular, at excess pressure of carbon dioxide formed during the dissociation of carbonates of alkali and alkaline earth metals, in particular calcium and sodium. In the case of such a mixed composition of carbonates, the dissociation of carbonates begins at a low temperature of 800-1100 ° C, and thus bubble bubbling is ensured.

It should be emphasized that the flux foamed due to the decomposition of the carbonates included in the proposed material is fundamentally different in the degree of dispersion of the phases and in the porosity of the same material, if it is purged using the traditional inert gas technology (argon). In addition, the foam has a different structure and an order of magnitude higher viscosity. It was experimentally established that the metal-salt foam from the melt has a porosity of about 90% with a high dispersion of pores (bubble diameter of 1-10 mm), which cannot be obtained by blowing with an inert gas when separate discrete bubbles float.

Obviously, the pressure in the foam bubble should be relatively stable, which is regulated by the amount of carbonates introduced into the filler. Moreover, it should exceed the sum of atmospheric and hydrostatic pressures of the metal in the bucket.

If the material contains 5-20 wt.% Carbonates, carbon dioxide is formed in the amount of 8-40 ncm ³ / g of the introduced material, which ensures its good foaming. At a lower content, foaming is not enough; at a higher content, splashes of metal from the bucket may occur.

The foaming intensity can be further changed by additionally introducing carbon in the composition of the material in an amount of 0.25-0.35 fractions of the proportion of carbon dioxide in carbonates. In this case, the decomposition of carbonates leads to the formation of carbon monoxide — CO, an active reducing agent, and a foaming gas.

3. The choice of constituent components of the material used, in particular, as a filler of cored wire, is due to the following. Like alkaline earth metals 2A, subgroups of the periodic system, alkali metals (sodium, potassium, etc.) are extremely active and react with most harmful impurities of steel: sulfur, phosphorus, non-ferrous, gases (oxygen, nitrogen, hydrogen, carbon monoxide, etc.). e.) with the formation of simple and complex compounds, salts, etc., including in the form of liquid inclusions and volatile compounds. They are characterized by: high refining ability, low specific gravity, low melting and boiling points.

Alkali metals and their salts are not yet actively used in ferrous metallurgy, in contrast to non-ferrous and rare metals metallurgy. The reason for this is their extreme activity, pyrophoricity of reactions occurring at temperatures of their introduction into the iron-carbon melt, as well as their insolubility in iron. The use of alkali metals in the form of metal powders is unsafe, not technologically advanced and difficult to implement.

It is proposed to use them in the form of fluxes - alloys of halides of alkali and alkaline earth metals, as well as carbonates, such as sodium and calcium. The latter provides several advantages:

- at ratios of halides close to the eutectic composition, fluxes melt directly in the steel shell - when the flux-cored wire is heated during the introduction of the material into the steel ladle;

- fluxes are characterized by high wettability and destroy film formations on the surface of reagents, improve contact between them and intensify diffusion processes;

- fluxes dissolve high-temperature fluoride compounds to obtain a salt composition capable of foaming under the influence of excessive gas pressure (carbon oxides, halide vapor). In this case, the adhesive properties of the melts are achieved, sufficient, on the one hand, to obtain and stabilize a refining gas-bubble structure, and, on the other hand, for the extraction of impurities and non-metallic inclusions from the molten liquid into the foam mass, followed by their removal into slag;

- fluxes melt as eutectic mixtures, but evaporate and dissociate not azeotropically. Therefore, chlorine and / or fluorine ions formed at intermediate stages of salt decomposition over a wide range of the existence of an emulsified foam modifier destroy the films of oxides, oxysulfides, etc., formed on the surface of the bubbles, and, thereby, catalyze the processes of melt refining and slag inclusions.

In quantitative terms, the lower limit of the content of the low-temperature component of the flux is determined by the sufficiency for a) foaming the refining composition and b) the solubility of the high-temperature metal-flux component. It was experimentally established that the minimum volume of the eutectic alloy should be at least 5 wt.% Of the total content of the filler material. Otherwise, the liquefaction of the material occurs slowly and the state of complete dispersion is not reached. The upper limit of 50 wt.% Low temperature fluxes provides sufficient fluidity, but limits the content of other components, in particular carbonates, necessary for foaming the material in the melt.

With regulated amounts of components is achieved:

1. A sufficient duration of the process of interaction with the metal — the “survivability” of the modifier increases — the thermal dissociation of flux-forming ingredients occurs in an extended time interval. This, obviously, is the result of capillary thermoconcentration instability of real flux melts, manifested, in particular, in the detectable duration of the evaporation-boiling periods:

for CaCl ₂ : 1200-1600 ° С, for CaF ₂ : 1580-2500 ° С.

2. The appearance of vapor-gas protection of the melt from saturation with gases from the atmosphere. We emphasize that halides are characterized by the highest propensity to bind hydrogen with the formation of compounds (such as HF, HCl, etc.), insoluble in the molten iron. Practice has shown that the presence of dissociating flux salts in the slag provides effective protection against gas saturation of the metal, preventing the penetration of oxygen, nitrogen, and hydrogen through the main slag layer in the ladle.

3. Protection of grain boundaries during their enrichment with calcium (the decay product of CaCl ₂ ) from the embrittling effect of horophobic precipitates and film phases - displacing them from the boundaries. To achieve this effect, the flux content in the material should be 5-50 wt.%. The lower limit is associated with the sufficiency of segregation enrichment of the boundaries with calcium, the upper limit is the need to introduce calcium or silicocalcium into the material.

It was experimentally established that, without decreasing its efficiency, the material composition may include, along with low-melting flux, other halide salts, in particular aluminum chloride (AlCl ₃ ) and / or cryolite (Na ₃ AlF ₆ ) in an amount of 3-10 wt. %

The additional introduction of calcium oxide in an amount of 2-15 wt.% In the composition of the material can enhance its refining properties. At high contents, the proportion of other components in the material decreases and the quality of the finished metal decreases.

An additional introduction of barium strontium carbonate into the composition of the material makes it possible to simultaneously have substances in the composition of the material that expand the temperature-time interval of its interaction with the melt and provide foaming of the introduced material. It has been established that the effect of its introduction on the quality of the material is noticeable starting from 5 wt.%, And when the content is more than 30 wt.%, The proportion of other components in the material decreases and the plastic and impact properties of the finished metal decrease.

The introduction of ferrosilicobarium and / or alumina in the composition of the material is due to the following circumstances. Calcium and barium form among themselves an unlimited solid solution, the melting / boiling points of calcium and barium are 848/1487 ° C and 725/1637 ° C, respectively. Barium practically does not boil in steel and, therefore, being in the melt for a longer time, barium in combination with calcium has a stronger refining and modifying effect, interacting with gases and impurities dissolved in the metal. The effect of the presence of barium in the composition of the material is positively manifested, starting with a content of ferrosilicobarium and / or alumobarium of 3 wt.%. An increase in the amount of data in the material, comprising more than 30 wt.%, Reduces the proportion of calcium, which negatively affects the spillability of the metal.

An example implementation of the method.

The claimed material was used during out-of-furnace processing under industrial conditions of steel melts of the St20 grade, having the composition, wt.%: 0.13-0.14С; 0.4-0.42 Mn; 0.15-0.17 Si; 0.025-0.027 S; 0.017-0.019 P; 0.12 C; 0.10 Ni; 0.15 Cu;

0.02Al; Fe is the rest. Material for steel refinement and modification was prepared by mixing in various proportions the following ingredients: 30% silicocalcium, metallic calcium, 22% silicobarium, fused flux containing 25% NaCl and 75% CaCl ₂ (composition A) or 80% CaCl ₂ and 20% CaF ₂ (composition B), AlCl ₃ , Na ₃ AlF ₆ , CaCO ₃ , Na ₂ CO ₃ , barium strontium carbonate, CaO and carbon (see table 2). These mixtures were crushed to a fraction of less than 2 mm and rolled into a flux-cored wire with a diameter of 14 mm.

When processing the melt according to the prototype, 30% silicocalcium was used, which also, after crushing to a fraction of 0-2 mm, was rolled into a flux-cored wire with a diameter of 14 mm.

Each ladle of steel using a tribamer was treated with cored wire, which had a certain composition of the filler - table 2. The filler consumption in the case of the claimed compositions of the material was 0.8 kg / t of steel, and with the composition of the prototype 1 kg / t of steel.

After treating the melt with flux-cored wire, steel was poured onto a high-grade continuous casting machine on a square of 100X100 mm, then rolled onto a 10 mm circle, in which contamination with nonmetallic inclusions, the proportion of globular HB, the elongation and impact strength of the metal were evaluated (see table 3).

The results shown in tables 2 and 3 indicate:

1. The processing of the melt material, according to the prototype, leads to the production of a metal characterized by high pollution by oxides (1.5 points) and sulfides (1.2 points), a low proportion of globular particles (58%), a small elongation (28%) and low impact strength (1.6 kgf * m / cm ² ) - var. 1.

2. The processing of the melt with a material with a composition according to claim 1 of the claims of the invention leads to a decrease in the content of oxides (not more than 1.05 points) and sulfides (less than 1 point), increases the fraction of globules (more than 70%), relative elongation ( not less than 35%) and impact strength (more than 2.2 kgf * m / cm ² ) - var. 3-5, 8, 10,15,16.

3. The processing of the melt by a material having a composition different from claim 1 of the claims of the claimed invention reduces the purity of the metal by inclusions, the fraction of globules, elongation and toughness - var. 2, 9, 28, 29.

4. The processing of the melt material, with the composition, according to claim 2 of the claims of the claimed invention, also leads to the production of metal of improved quality, compared with the use of the material of the prototype var. 6 and 7.

5. The processing of the melt material, with the composition, according to claim 3 of the claims of the claimed invention, similarly leads to the production of metal of improved quality, compared with the use of the material of the prototype - var. 11, 12.

6. The processing of the melt material, with the composition, according to PP.4-5 of the claims of the claimed invention, also leads to the production of metal of improved quality, compared with the use of the material of the prototype - var.13, 14, 17.

7. The processing of the melt material, with the composition, according to PP.6-9 of the claims of the claimed invention, similarly leads to the production of metal of improved quality, compared with the use of the material of the prototype - var. 18-21.

8. The processing of the melt material, with the composition, according to PP.10-17 of the claims of the claimed invention, also leads to the production of metal of improved quality, compared with the use of the material of the prototype - var.22-27.

Thus, the presented results indicate that the processing of the melt by the claimed method using the inventive material leads to an increase in the temperature-time interval of the interaction of the material with the melt, as well as an increase in the efficiency of the interaction of the melt with the material. This provides an increase in the quality of steel while reducing the consumption of material for refining and modifying the treatment of iron-carbon melt.

table 2 The compositions of the tested materials filler flux-cored wire No. p / p The composition of the material of the filler cored wire, wt.% The total content of SiCa and Ca _met SiBa content The composition of the eutectic flux AlCl ₃ Na ₃ AlF ₆ The total content of CaCo ₃ and Na ₂ CO ₃ Soda CaO Sod Soda barium carb. BUT B 1 prototype one hundred - - - - - - - 2 twenty - fifty - - - thirty - 3 thirty - - fifty - - twenty - four thirty - fifty - - - twenty - 5 45 - - 45 - - 10 - 6 27 3 fifty - - - twenty - 7 fifteen thirty 45 - - - 10 - 8 45 - 40 - - - fifteen - 9 twenty - 60 - - - twenty - 10 45 - - 40 - - fifteen - eleven 32 5 45 - 3 - fifteen - 12 35 - - 40 - 10 fifteen - 13 33 - fifty - - - fifteen 2 fourteen 25 10 - 40 - - 10 fifteen fifteen 70 - 25 - - - 5 - - 16 75 - 5 - - twenty - - 17 thirty - - 40 - 10 fifteen 5 - - eighteen 16.7 - fifty - - - thirty - 3.3 - 19 13.5 thirty - 45 - - 10 - 1,5 - twenty 28.7 5 thirty - 3 - thirty - 3.3 - 21 23.5 10 - 40 - - 10 fifteen 1,5 - 22 18.5 - fifty - - - thirty - - 1,5 23 24 - - fifty - - twenty - - 6 24 24 3 47 - - - twenty - - 6 25 21 3 - 47 3 - twenty - - 6 26 26 - 40 - - 3 twenty 5 - 6 27 27.5 3 45 - 5 - 10 5 1,5 3 28 85 - - 12 - - 3 - - 29th 85 - 10 - - - 3 2 -

Table 3 The influence of the composition of the material of the filler cored wire on non-metallic inclusions mechanical properties of steel No. p / p Inclusion pollution, point The proportion of globular particles,% Relative extension, % Impact strength KCV _{-60 ° C} , kgf * m / cm ² Note Oxides Sulfides 1 prototype 1,5 1,2 58 28 1,6 2 1.3 1,2 70 thirty 1.7 pyroelectric effect 3 1.05 0.9 75 36 2,3 four 1.00 0.9 76 35 2,3 5 1.05 0.9 75 36 2,4 6 1.00 0.85 77 37 2,5 7 0.95 0.9 75 36 2,5 8 0.95 0.9 77 37 2.6 9 1.3 1,2 58 28 1,6 10 0.95 0.95 78 36 2,5 eleven 1.00 0.95 76 36 2,4 12 0.95 0.9 77 37 2,5 13 1.05 0.95 74 36 2,4 fourteen 1.00 0.95 75 35 2,5 fifteen 0.9 0.95 74 37 2,5 16 1.05 0.95 74 35 2,3 17 1.00 0.95 74 35 2,4 eighteen 0.95 0.9 76 36 2,5 19 0.95 0.95 75 34 2,4 twenty 0.95 0.9 77 35 2.6 21 0.9 0.85 77 36 2.7 22 1,0 0.95 75 35 2.6 23 0.95 0.9 77 37 2.6 24 0.95 0.9 76 36 2.6 25 0.9 0.85 76 36 2.7 26 0.9 0.9 75 36 2.7 27 0.9 0.85 76 37 2.6 28 1.4 1,2 57 29th 1,5 29th 1.45 1,2 57 28 1,5

Claims (21)

1. Material for processing an iron-carbon melt, including a calcium-containing substance in the form of a mixture of calcium in the metal phase and an alloy of calcium with silicon, characterized in that it further comprises a low-melting flux of alkali and / or alkaline-earth metal halides and alkali and / or alkaline-earth metal carbonates at the following ratio of components, wt.%:
fusible flux 5-50 carbonates 5-20 calcium substance rest 2. The material according to claim 1, characterized in that it further comprises silicobarium and / or alumina in an amount of 3-30 wt.%. 3. The material according to claim 1 or 2, characterized in that it further comprises aluminum chloride (AlCl ₃ ) and / or cryolite (Na ₃ AlF ₆ ) in an amount of 3-10 wt.%. 4. The material according to claim 1 or 2, characterized in that it further comprises calcium oxide in an amount of 2-15 wt.%. 5. The material according to claim 3, characterized in that it further comprises calcium oxide in an amount of 2-15 wt.%. 6. The material according to claim 1 or 2, characterized in that it further comprises carbon in an amount of 0.25-0.35 fractions of the proportion of carbon dioxide in carbonates. 7. The material according to claim 3, characterized in that it further comprises carbon in an amount of 0.25-0.35 fractions of the proportion of carbon dioxide in carbonates. 8. The material according to claim 4, characterized in that it further comprises carbon in an amount of 0.25-0.35 fractions of the proportion of carbon dioxide in carbonates. 9. The material according to claim 5, characterized in that it further comprises carbon in an amount of 0.25-0.35 fractions of the proportion of carbon dioxide in carbonates. 10. The material according to claim 1 or 2, characterized in that it further comprises a concentrate of barium strontium carbonate in an amount of 5-30 wt.% Of the amount of carbonates. 11. The material according to claim 3, characterized in that it further comprises a concentrate of barium strontium carbonate in an amount of 5-30 wt.% Of the amount of carbonates. 12. The material according to claim 4, characterized in that it further comprises a concentrate of barium strontium carbonate in an amount of 5-30 wt.% Of the amount of carbonates. 13. The material according to claim 5, characterized in that it further comprises a concentrate of barium strontium carbonate in an amount of 5-30 wt.% Of the amount of carbonates. 14. The material according to claim 6, characterized in that it further comprises a concentrate of barium strontium carbonate in an amount of 5-30 wt.% Of the amount of carbonates. 15. The material according to claim 7, characterized in that it further comprises a concentrate of barium strontium carbonate in an amount of 5-30 wt.% Of the amount of carbonates. 16. The material of claim 8, characterized in that it further comprises a concentrate of barium strontium carbonate in an amount of 5-30 wt.% Of the amount of carbonates. 17. The material according to claim 9, characterized in that it further comprises a concentrate of barium strontium carbonate in an amount of 5-30 wt.% Of the amount of carbonates. 18. The material according to claim 1, characterized in that the low-melting flux is a eutectic composition flux. 19. The material according to claim 1, characterized in that the material is a filler for cored wire. 20. A method of treating an iron-carbon melt by foaming, characterized in that the melt is foamed by introducing a material according to any one of claims 1-19. 21. The method according to claim 20, characterized in that the foaming is carried out with carbon dioxide formed during the decomposition of the material introduced into the melt in a volume of 8-40 ncm ³ / g.