UA121604C2 - STRUCTURAL STEEL WITH BAINETIC STRUCTURE, FORGED PARTS MADE FROM IT, AND METHOD OF OBTAINING THE FORGED PART - Google Patents

Abstract

The invention provides a steel that has increased strength, without the need to perform complex heat treatment procedures, and which also has a low tendency to deformation. For this purpose, structural steel according to the invention includes, wt. %: up to 0.25 C, up to 0.45 Si, 0.20-2.00 Μn, up to 4.00 Cr, 0.7-3.0 Mo, 0.004-0.020 Ν, up to 0.40 S, 0.001 -0.035 Αl, 0.0005-0.0025 V, up to 0.015 Nb, up to 0.01 Ti, up to 0.10 V, up to 1.5 Ni and up to 2.0 Cu, residual iron and permanent impurities, where the content of Al%Al, the content of Nb%Nb, the content of Ti%Ti, the content of V%V and the content Ν%Ν of structural steel in each case meet the following condition: %Al/27 + %Nb/45 + %Ti/48 + %V/25 > %N/3.75. Structural steel according to the invention has a yield strength of at least 750 MPa, a tensile strength of at least 950 MPa and a structure that includes at least 80 vol. % of bainite and in total a maximum of 20 vol. % residual austenite, ferrite, pearlite and/or martensite. Due to its profile characteristics, the steel according to the invention is particularly suitable for obtaining by forging methods forged parts having large changes in the cross-section along their length. The invention also discloses a method of obtaining such forged parts.

Description

suitable for obtaining by forging methods forged parts that have large changes in the cross-section along their length.

The invention also discloses a method of obtaining such forged parts.

The invention relates to structural steel with increased strength and structure, containing at least 80 vol. 95 bainite.

The invention also relates to a forged part obtained from such structural steel.

Finally, the invention relates to a method of obtaining a forged structural steel part according to the invention.

Where, in the following description, details of alloys or other steel compositions are given in "95", in each case they belong to the mass, unless the contrary is clearly indicated.

All mechanical properties stated herein for steels according to the invention and any steels given for comparison, unless otherwise stated, have been determined in accordance with SIM

EM IBZO 6892-1.

As Oiri--Etc. Spgivtors Keshi ey a). reports in the article "EpimisKiipd eipeb5 PposptTevivyep. dikshShep

Baiipyizspep (NOV) stages of tOg pospreapzrgistie Zspitiedebashtsieiye" |OemeIortepi oi a podp-5igepdiy, disshe, Baiipyis (NOV) vieee!i og Pidnpiu-zitebz5zei Togdey sotropepiv)|, appearing in Zsptiede-

Washigpai, issue of September 2010, published by Ipdivigiemegrapa Mazzimitiogtypod E.M., it is in the forging industry that there is a demand for steel material concepts that offer the possibility of achieving increased strength and plasticity and at the same time short technological chains for their production. The article also states that in this regard, the prospect was to show materials with a bainitic structure, in which good properties of strength and plasticity are combined with the absence of the need for additional heat treatment, characterized by a tensile strength of more than 1,200 MPa, a yield strength of more than 850 MPa and elongation at break by more than 10 95 with an impact energy of the specimen with a cut of 27 J at room temperature temperature As an example of alloy concepts, the following properties are offered, the article presents steel with (in mass 95) 0.18 C, 1.53 5, 1.47 Mp, 0.007 5, 1.30 St, 0.07 Mo, 0.0020 B, 0.027 MB, 0.26 Ti, 0.0080 M, residual iron and permanent impurities and steel with 0.22 C, 1.47 51, 1.50 Mp, 0.006 5, 1.31 St, 0.09 Mo, 0.0025 V, 0.035 MB, 0.026 Ti, 0.0108 M, residual iron and permanent impurities

Another development, which is also aimed at steel for obtaining stamped parts, which without additional heat treatment have increased strength and at the same time high plasticity, is described in EP 1 546 426 VI. The steel known from this description of the patent contains (in mass

Zo Fe) 0.12-0.45 C, 0.10-1.00 5, 0.50-1.95 Mp, 0.005-0.060 5, in each case 0.004-0.050 AI and Ti, in each case up to 0 ,60 St, Mi, So, MU, Mo and Si, up to 0.01 V, up to 0.050 MB, . 9oAI; the content of MO 955 and the content of Ti 95Ti correspond to the condition of 1.6 x choe--1.5 x UbAI--2.4 x 95Mr--1.2 x 96Ti - 0.040-0.080 wt. 95 and the content of Mp 95Mp, the content of St 95St, the content of Mi domi, the content of Cy 90Cy and the content of Mo 95Mo correspond to the condition 1.2 x 96Mpy--1.4 x 95St1--1.0 x 95Mi-1.1 x

FobSy-1.8 x 90Mo - 1.00-3.50 wt. 95.

In this document, it is considered essential that the necessary improvements in ductility are achieved by reducing the carbon content of steel. The substantial loss of strength that accompanies this is, according to the prior art, balanced by conventional alloys of elements whose content is matched in such a way that it is strengthened by the mixed results of crystal formation.

In addition, from OE 697 28 076 T2 (ER 0 787 812 VI) a method of obtaining a forged steel part is known, in which steel with (in mass 95) 0.1-0.4 C, 1-1.8 My, 0 ,15-1.7 5I, up to 1 Mi, up to 1.2 St, up to 0.3 Mo, up to 0.3 M, up to . up to 0.006 calcium, up to 0.03 Te, up to 0.05 5e, up to 0.05 Vi and residual iron and permanent impurities are cast in the form of a billet of continuous pouring, which is hot-forged in the usual way for the production of a forged part. The forging is then subjected to heat treatment, which involves cooling at a cooling rate Mg greater than 0.5 "C/s from the temperature at which the steel is austenitic to a temperature Tt between M5 4100 "C and

M5 -20 "С. The forged part is kept for at least two minutes at a temperature between the temperature Tt and the temperature Ti, for which TI » Tt -100 "С is used. Thus, the intent is to obtain a steel component substantially of a bainite structure comprising at least 15 95 lower bainite and preferably at least 20 95 bainite formed between Tt and t.

Practical tests with steel materials of the type described above have shown that such bainitic steels are unsuitable for components with large changes in cross-section due to their tendency to deformation and strong fluctuations in mechanical characteristics.

Instead of these prerequisites for the creation of the invention, the task of the invention was to provide a steel with increased strength, without the need to perform complex heat treatment procedures, with a low tendency to deformation and which in itself is particularly suitable for the production of forging methods of forged parts with substantial changes in the transverse section along their length.

The intention is to similarly point to a forged part that has an optimal combination of properties without complex heat treatment processes.

Finally, the intention is to propose a method of obtaining a forged part, which allows, with the help of simple means, to create forged parts with an optimal combination of properties.

In relation to steel, the invention solved the above problem with structural steel specified in point 1.

In relation to the forged part, the solution according to the invention to the above task is to obtain such a steel component from the steel according to the invention.

In conclusion, with regard to the method, the invention solved the above-mentioned task in that the steps of the method mentioned in point 13 are carried out during the production of the forged part.

Advantageous forms of the invention are given in the dependent claims and will be explained in detail in the following description together with the general idea of the invention.

Structural steel according to the invention has a yield strength of at least 750 MPa and a tensile strength of at least 950 MPa and at least 80 rev. 95 of the bainite structure, in which the remaining 20 vol. 95 structures can be residual austenite, ferrite, pearlite or martensite.

In this document, the steel according to the invention is characterized by an increased elongation at break A of at least 10 95, in particular at least 12 95, where in practice it has been shown that steels according to the invention usually achieve an elongation at break A of at least 15 95.

According to the invention, structural steel thus contains (in mass 90) up to 0.25 C, up to 1.5 5i, in particular up to 1 5i or up to 0.45 51, 0.20-2.00 Mp, up to 4.00 St, 0.7-3.0 Mo, 0.004-0.020 M, up to 0.40

C, 0.001-0.035 AI, 0.0005-0.0025 V, up to 0.015 MB, up to 0.01 Ti, up to 0.50 M, up to 1.5 Mi, up to 20 Sp and residual iron and permanent impurities, where the content AI 95AI, MO content 95MB, Ti content 9oTi, M content 95M and the content of M 90M structural steel in each case corresponds to the following condition:

FfoAI/2 7 io Mr/45--95 G/48--95M/25590M/3.75

Permanent impurities, which are obtained as a result of production, include all

Of the elements, which, taking into account their properties of interest, are present here in quantities that do not affect the alloying process, as well as due to the technological route of steelmaking or the corresponding selected source material (waste of metal production) found their way into steel. Permanent impurities also include, in particular, P content up to 0.0035 wt. 95.

The steel according to the invention and the forged parts obtained from it can be characterized by a particularly uniform distribution of properties, even if, due to the variety of component sizes, very different localized cooling conditions prevail during cooling from the forging heat considered through the volume of the forged part. This insensitivity to cooling conditions is achieved by the fact that the structural steel according to the invention has a homogeneous, as far as possible, exclusively bainite structure with a low variation in hardness. This homogeneous microstructure at the same time has a low internal tension, which positively affects the technological mode of shunting.

Therefore, the steel according to the invention is particularly suitable for the production of forged components, in which areas with very different volumes and diameters are opposed to each other.

Examples of such forged parts, for the manufacture of which the use of steel forging methods according to the invention is particularly suitable, are crankshafts, pistons and the like, intended, in particular, for internal combustion engines.

In addition, parts in the area of the chassis and wheel suspension with very different cross-sections can be reliably obtained from steel according to the invention without extensive further processing by means of grinding, while maintaining predetermined strength characteristics.

As will be clear from the time-temperature diagram attached as Fig. 1 of the steel according to the invention, from a material technology point of view, this means that with the structural steel according to the invention, a particularly wide window for bainite treatment can be applied if the structural steel according to the invention is continuously cooled by forging heat. At the same time, the structural steel alloy according to the invention is selected in such a way that during cooling none of the amounts of martensite or ferrite and/or pearlite, which affect its properties, leads to a structure. Structural steel according to the invention is one that differs in that it has mainly, that is, at least up to 80 vol. 95, a bainite structure, where the content of non-bainite structural components in steels according to the invention is generally minimized to such an extent that the steel according to the invention has a completely bainite structure in the technical sense.

Here, with the structural steel according to the invention, the bainite has as nearly a constant hardness as possible regardless of the cooling rate. Permanent hardness is the result of almost complete transformation of what was previously austenite into bainite, mainly at the stage of bainite transformation.

Limiting the content of C to a maximum of 0.25 wt. 95 means, on the one hand, that the structural steel according to the invention, despite the maximum strength, has the properties of good stretching and plasticity. In the steel according to the invention, the low content of C also contributes to the acceleration of the transformation of bainite, which allows to avoid the development of undesirable structural components.

At the same time, nevertheless, a certain amount of carbon in the structural steel according to the invention can also contribute to the strength. For this purpose, a content of at least 0.09 wt. 95 C in steel. Thus, the optimal effect of the presence of C in steel according to the invention can be achieved when the content of C is adjusted to 0.09-0.25 wt. 95.

The content of 5i steel according to the invention is limited to 1.5 wt. 95, in particular 1 wt. 95 or 0.5 wt. 95 to allow the bainite transformation to occur as early as possible. To be particularly sure of achieving this effect, the content of 5i can also be limited to a maximum of 0645 wt. 95.

Mo is present in structural steel according to the invention, with a content of 0.6-3.0 wt. 95 to delay the transformation of the structure into ferrite or pearlite. This effect takes place, in particular, if at least 0.7 wt. 95, in particular more than 0.70 wt. 96 Mo. For a content of more than 3.0 wt. 95 a further economically beneficial increase in the positive Mo effect takes place in the steel according to the invention. Apart from this, above 3.0 wt. 95 Mo there is a danger of the formation of a carbide phase enriched in molybdenum, which can negatively affect the plasticity properties. The optimal effect of Mo in steel according to the invention can be expected if the Mo content is at least 0.7 wt. 95. Here, the maximum Mo content is 2.0 wt. 95 was particularly effective.

Manganese is present with a content of 0.20-2.00 wt. 95 in steel according to the invention, in order to

Zo to adjust the tensile strength and yield strength. The minimum content is 0.20 wt. 95

MP is necessary to achieve an increase in strength. If it is planned to achieve this effect 3, in particular reliability, then the Mn content of at least 0.35 wt. 95. An excessively high content of Mn leads to delays in the transformation of bainite and thus to predominantly martensitic transformations. The MP content is thus limited to a maximum of 2.00 wt. 95, in particular 1.5 wt. 95. Negative effects from the presence of Mn can be especially reliably avoided by limiting the content of Mn in the steel according to the invention to a maximum of 1.1 wt. 95.

The sulfur content in steel according to the invention can be up to 0.4 wt. 95, in particular a maximum of 0.1 wt. 95 or a maximum of 0.05 wt. 95, to maintain the machinability of steel.

Accurate adjustment of fusion methods, taking into account the mechanical properties and microstructure of structural steel according to the invention, takes place according to the concept of fusion according to the invention using combined microfusion of boron elements with a content of 0.0005-0.0025 wt. 95, nitrogen with a content of 0.004-0.020 wt. 95, in particular at least 0.006 wt. 95 M or up to 0.0150 wt. 95 M, aluminum with a content of 0.001-0.035 wt. 95 and niobium with a content of up to 0.015 wt. 95, titanium with a content of up to 0.01 wt. 95 and vanadium with a content of up to 0.10 wt. 95.

In this document, the contents of 9BAI, 95Мб, 95, 90М and 90М and АЙ, МБ, Ти, М and М are related to each other by the condition

FfoAI/2 7 io Mr/45--95 Г/48--95М/25590М/3.75 so that the nitrogen contained in structural steel, due to the corresponding content of AI, and the necessary content of MB, Ti and M, which also are added, are fully bound, and boron can thus have a conversion-retarding effect. At the same time, the content of trace elements provided according to the invention and balanced with each other, and the content of M contributes to the increase of fine-grained stability and strength.

Binding according to the invention M also allows boron to be effective as a dissolved element in the matrix and inhibits the formation of ferrite and/or pearlite.

To reliably provide an advantage with microalloying elements and aluminum, it may be appropriate to set the content of A at least 0.004 wt. 95, containing Ti at least 0.001 wt. 95, with an M content of at least 0.02 wt. 95 or MO content of at least 0.003 wt. 95. Here the elements of microalloying MU, Ti and MB, on the one hand, and AI, on the other, in each case can be present in combination with one or more elements of the group "AI, M, Ti, Mr" or separately in the amount that exceeds the specified minimum content.

For content up to 0.008 wt. 95 Those, up to 0.01 wt. 95 MB, up to 0.075 wt. 95 M or up to 0.020 wt. 95 AI, the action of these elements in structural steel according to the invention can be applied to particularly good effect. At the same time, the formed nitrides or carbonitrides lead to increased strength and contribute to fine-grained stability. Here too, the specified upper limits of the content of Ti, ME, M or AI in each case individually or in combination with each other can be observed in order to achieve the optimal effect of the corresponding alloying element.

The content of St up to 4.00 wt. is not necessarily present. 95, in particular to Z mass. 95 or up to 2.5 wt. 95, contributes to the durability and corrosion resistance of the steel according to the invention. For this purpose, as an example, at least 0.5 wt. 95 or at least 0.8 wt. 95 Sg.

Similarly, an optional Mi content of up to 1.5 wt. 9o can also contribute to the hardening of steel.

The alloy elements that reach the steel according to the invention with the help of the starting material or intentionally added alloy elements also include Si, the content of which, in order to avoid negative effects in the steel according to the invention, is limited to a maximum of 2.0 wt. 95. The positive effect of the optional presence of copper in the process of alloying structural steel according to the invention consists in the formation of the thinnest films of residual austenite and the associated significant increase in the level of plasticity. This effect can be achieved if at least 0.3 wt. 95 Cy, in particular, more than 0.3 wt. 95 Si present in structural steel according to the invention. Limiting the C content to a maximum of 0.9 wt. 95; an optimized positive effect of the copper content can be achieved.

If the steel according to the invention is heated to high temperatures characteristic of hot work, at least 100 "C above the corresponding temperature Ac3, in particular a heating temperature of more than 900 "C for hot work, then hot worked and finally cooled in a controlled or unregulated manner under still air or an air jet to a temperature of less than 200 "С, in particular to room temperature, then in an extremely wide range of cooling rates after the transformation, the same bainite structure The temperature of AsZ3 steel can be determined by a known method at

Based on its corresponding composition. The upper limit of the heating temperature range is usually 1300 "C, in particular 1250 "C or 1200 "C.

To measure the range of cooling rates, a time of 18/5 can be applied here, thus the time spent on the relevant part in the hot state to cool from 800 "C to 500 "C. For cooling components made from steel according to the invention, this time 18/5 should be 10-1,000 s.

The cooling time selected in each case should be selected based on the corresponding heating temperature. The effect of heating temperature can be understood from the time-temperature diagram attached as Fig. 2, in which for heating temperatures of 900 "C (solid line), 1100 "C (dashed line) and 1,300 "C (dotted line) the corresponding position of the corresponding range of bainite displayed due to the cooling time. Accordingly, at low heating temperatures of 900 "C, a shorter time of 18/5 should be chosen to achieve the desired bainite structure, while at higher heating temperatures cooling may be slower. At heating temperatures in the range of 900-1300 "C and, accordingly, if the 18/5 time is 100-800 s, for the steel according to the invention there is a high probability that during cooling of the steel according to the invention the bainite range will be reached regardless of appropriate heating temperature.

The concept of the alloy according to the invention thus allows high temperatures during hot treatment of more than 1500 "C, as a result of which the forces of plastic deformation during hot treatment can be reduced without the undesirable occurrence of grain growth.

The method according to the invention for obtaining forged parts with a yield strength of at least 750 MPa and a tensile strength of at least 950 MPa and at least 80 vol. 905 by the bainite structure, which may include a total of up to 20 vol. 95 residual austenite, ferrite, pearlite or martensite, includes the following stages of the method: a. providing a billet of continuous casting for forging, comprising structural steel with a composition, in accordance with the invention, as explained above; b. heating the billet of continuous pouring for forging to the forging temperature at least 100 "C higher than the temperature As3Z of the corresponding structural steel, where the temperature

AsZ is determined in the usual way as a function of the corresponding composition of the structural steel; in. forging of a billet of continuous pouring for forging, heated to the temperature of forging into a forged part;

Mr. cooling the forged part from the forging heat to a temperature below 500 "C, where 18/5 - the cooling time is 10-1,000 s.

In order to reduce the forces of plastic deformation in the course of the method according to the invention to minimize the necessary efforts of hot volumetric stamping, it can be advantageous if the corresponding billet of continuous casting, representing the starting point of forging, is heated to a forging temperature of more than 1150 70.

Further adjustment of the mechanical properties, in particular the strength and plasticity of the components subjected to hot treatment, in particular forged, made of steel, according to the invention, can take place with the help of the tempering heat treatment process, during which the corresponding part is kept for 0.5-2 hours in a temperature in the range of 180-375 "C.

In practice, the steel according to the invention has a tensile strength of at least 950 MPa, a yield strength of at least 750 MPa, and an elongation at break A of at least 15 95, while it has been shown in practice that even higher elongation of A of at least 17 95. This combination of features in forged parts containing steel according to the invention is present, in particular if they are created by the method according to the invention.

In the following description, the invention will be explained in more detail by means of examples.

E1-Eb steel melts, according to the invention, and comparison of the M1 melt with the compositions shown in Table 1, were melted and poured into a billet of continuous pouring, which includes blocks, as a rule, made available for further processing, using forging methods.

Continuous casting blanks are heated for forging deformation to the heating temperature Tm/u, then conventionally hot-worked using stamping to produce forged parts, and then cooled to room temperature in air. With some of the resulting forged parts, tempering is then performed.

Table 2 shows the heating temperatures Tmu given in the examples, the time 18/5 required in each case to pass through the critical temperature range of 800-500 7C, the temperature and duration of tempering heat treatment where it was actually implemented, as well as the proportion of bainite in the structure, tensile strength Kt, yield strength Ke, length A and

Z is the impact energy of a sample with a MU cross-section of a forged part obtained after forging.

The examples show that, when the technical requirements are met, according to the invention, forged parts can be obtained that allow the operating parameters set during their creation to be changed over a wide range, and, acting in this way, it is possible to obtain hot-worked components with optimized mechanical properties.

Table 1 (Steel) with | 5|Mpo| st |mo| m | 5 | And | in | mi p | M|mys| RII 0 | 2 Te

SEZ T047102y|09011,7210,72| 0.0082 | 0.003 | 0.031 | 0.0008 | 0.007 | 0.001 10.03|0.2210.6210.017| 0002525 | 0.002187 | YES

Sat at ole1073|1491094|078|00077 00041027 00013 | 0003 |0.00110061 0211017 0016 0003488 | 0002050 | YES 6 GTom1910.6710.89|14710.79 00092 0.005 0.035 | 0.0012 | 0.003 G0.001 10.03 10.22 10.13 0.020 | 0.002584 | 0.002453 1 YES

Hm TogaTolo| t5o| 2001003 00100 10002023) - |oogo|oot5|0021omo 05010018 oogyaoe | osoyaveya | NO

Data in mass. 95, residual iron and permanent impurities (1): 96А/27 ФМ Б/45--90 ГИ/48--о6М/25 (2): 95М/3.75

Table 2

Heat-treated steel structure

PLUM mi Gotv|Bos| Missing | 7596(alyshokMe) | 1352 | 887 181 BUT "L

Claims (14)

FORMULA OF THE INVENTION 1. Structural steel having a yield strength of at least 750 MPa, a tensile strength of at least 950 MPa and a structure comprising at least 80 vol. 95 bainite and a maximum of 20 vol. 95 of residual austenite, ferrite, pearlite and/or martensite, where the steel contains, wt. 90: WITH. 0.09-0.25, z: 0-15, Mp: 0.20-2.00, Sg: 0-4.00, Mo: 0.7-3.0, M: 0.004-0.020, Z: 0-0.40, AI: 0.001-0.035, B: 0.0005-0.0025, M: 0-0.015, Ti: 0-0.01, U: 0-0.10, MI: 0-1.5, Сy: 0-2.0, residual iron and permanent impurities, and AI content - 95AI, MB content - 95M, Ti content - 9oTi, M content - 90M and M content - 96M structural steel in each case meet the following condition: 90A1/27--95Mr/45--95 Gi/48--907/25290М/3.75. 2. Structural steel according to claim 1, which differs in that the AI content in it is at least 0.004 wt. 95. 3. Structural steel according to any of the previous items, which differs in that the AI content in it is a maximum of 0.020 wt. 95. 4. Structural steel according to any of the previous items, which is characterized by the fact that the Mb content in it is at least 0.003 wt. 905. 5. Structural steel according to any of the previous items, which differs in that the Mb content in it is a maximum of 0.01 wt. 95. 6. Structural steel according to any of the previous items, which differs in that the Ti content in it is at least 0.001 wt. 905. 7. Structural steel according to any of the previous items, which differs in that the Ti content in it is a maximum of 0.008 wt. 95. 8. Structural steel according to any of the previous items, which differs in that the M content in it is at least 0.02 wt. 965. 9. Structural steel according to any of the previous items, which differs in that the content of M in it is a maximum of 0.075 wt. 905. 10. Structural steel according to any of the previous items, characterized in that its elongation at break A is at least 10 95. 11. A forged part comprising steel obtained according to any of the preceding clauses. 12. The method of obtaining a forged part having a yield strength of at least 750 MPa and a tensile strength of at least 950 MPa and at least 80 rev. 95 of the bainite structure, where the residual maximum is 20 vol. 96 other proportions of the structure can be residual austenite, ferrite, pearlite and/or martensite, which includes the following stages of the method: a) providing a billet of continuous pouring for forging, which includes structural steel with a composition according to any of claims 1-9; b) heating the billet of continuous casting for forging to a forging temperature of at least 100 "С above the temperature AsZ of the structural steel; c) forging the billet of continuous casting for forging, heated to the forging temperature, into the forged part; d) cooling the forged part from the forging heat to a temperature below 200 "С, where 18/5 - cooling time - is 10-1000 s. 13. The method according to claim 12, which differs in that the forging temperature is higher than 1150 "С. 14. The method according to claim 12 or claim 13, which differs in that, after cooling, the forged part is subjected to tempering by heat treatment, during which it is kept for 0.5-2 hours. at tempering temperature by heat treatment of 180-375 "С. Shchi uk "she 5 TV mini: so ee RN drnketyusresrnn yah shshn 3 11 ef run Za s GO KK oh i To KRB z" gh I i х ш ш х КО ч и и и ТИК и у I 5 tu o fen HU: ж х щи Х Х Ум Хмододеоноя и Ки и ТЕ: m s зову ky dae хх Х Х ИЗ ше ek : EE mae : RI still IA i ke m 1 Ko yuodsoyuvyutyuy, TI sha: KTK and BI KO shany st a TK TEN Deodnni nave. BE; Gi BIR BI s na dizhi M 1 Deco V i Ri IN A ZK KU eh OTAK her BI TB ok sche : IEE IZ EK h a sche M dovi Fe» 1 TIN ORI kh ek kkukicheinni NK: I ENAI k KAT Ko a zehfenndno EE BECAUSE NOT! Her 4: X bottom; I 5 KU Mo. 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