AU714663B2 - Nozzle for continuous casting of steel - Google Patents

Description

04821

SPECIFICATION

NOZZLE FOR USE IN CONTINUOUS CASTING OF STEEL Industrial Field of the Invention The present invention relates to a nozzle used in continuous casting of steel, such as a submerged nozzle, a long nozzle, etc.

Prior Art In the continuous casting of steel, conventionally, A1 2 0 3 -SiO 2 -C nozzles having superior resistance to spalling have been the most widely used. However, in the case where the nozzles made with A1 2 0 3 -SiO 2 -C material are used for the casting of aluminum killed steel, there arises a problem of blockage of the nozzle due to the adhesion of Al 2 03 inclusions in the molten steel. Also, in the case of using the above nozzles for casting high oxygen content steel, high manganese content steel or stainless steel, a problem conversely arises in which the nozzles are melt-damaged. The blockage or melt-damage of nozzles not only causes the deterioration of the service life of refractory materials, but also hinders the operation of steel manufacture and adversely affects the quality of steel materials. Accordingly, the development of a nozzle that is free from blockage and has melt-damage resistance for use in continuous casting of steel is of great importance.

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Under the circumstances, as a countermeasure to this, Japanese Patent Laid-open No. 3-243258 discloses a nozzle in which materials containing a) not less than 90% by weight of A1 2 0 3 O; b) not less than 90% by weight of MgO; or c) not less than 90% by weight of ZrO 2 are formed into cylindrical sleeves, and one or two of them are inserted in combination with each other to be used as a nozzle.

Further, Japanese Patent Laid-open No. 5-237610 proposes, for the purpose of decreasing the blockage of the nozzle, the use of a refractory material, as a material for an interior body of the submerged nozzle, in which respective contents of carbon and SiO 2 are less than 1% by weight, spinel content is 1 to 40% by weight, MgO content is 0.5 to 15% by weight, and the rest is Al20 3 Problems the Invention Aims to Solve The main mechanism that causes blockage of A120 3 -SiO 2

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nozzles in the casting of aluminum killed steel is as follows: Firstly, in a refractory at high temperature, reaction of the following Equation occurs between SiO 2 and C used as raw materials. SiO (gas phase, hereinafter referred to as and CO diffuse at the interface between the nozzle and molten steel, and reactions with Al in the molten steel occur in accordance with the following Equations and As a result, a network layer of alumina is formed on the working surface of the nozzle and melt-adhered onto the nozzle surface to initiate the adhesion of Al 2 0 3 infusions thereto. As the adhesion of Al 2 0, infusions progress, nozzle blockage will become worse.

SiO 2 C(s) SiO(g) CO(g) (1) 3SiO(g) 2A1 A1 2 0 3 3Si (2) 3CO(g) 2AJ A,10 3 3£ (3) In the above equations, represents solid phase, and Al, Si and C each represent the molten Al, Si and C in the molten steel.

On the other hand, the mechanism of melt-damage of A1 2 0 3 SiO 2 -C nozzle in the casting of high oxygen content steel, high manganese content steel or stainless steel is as follows: Firstly, carbon in the working surface of refractory material dissolves into the molten steel. That is, the following Equation is established, and the working surface is rendered into A1 2 0 3 -SiO-C oxide.

C C (4) Thereafter, Mn, Q, and Fe in the molten steel penetrate, in the form of MnO and FeO, into the working surface. That is, the following Equations and are established.

Mn Q (MnO) Fe Q (FeO) (6) Furthermore, MnO-FeO inclusions in the molten steel collide onto the working surface, and are adhered thereonto. The MnO and FeO that have penetrated into the working surface because of the above two reasons, react with A1 2 0 3 and SiO 2 in the working surface to form a liquid slag of A1203-SiO 2 -MnO-FeO. When the slag is lost in the stream of molten steel, the melt-damage of refractory material is caused.

However, the above-mentioned conventional nozzles are effective in some extent to prevent the blockage of nozzles but less effective in suppressing the melt-damage of nozzles. Conversely, some conventional nozzle may suppress the melt-damage of nozzles but not the blockage of nozzles.

Accordingly, an object of the present invention is to provide a nozzle for use in continuous casting of steel, which can overcome the above-mentioned problems, and is free from blockage and has melt-damage resistance.

Means for Solving the Problem According to the present invention there is provided a nozzle for use in continuous casting of steel, 9 characterized in that at least an interior surface of the nozzle and/or portions that come into contact with molten 9steel are of a refractory material consisting solely of a 20 mineral phase is composed of spinel, or spinel and periclase; a constituent element which is substantially composed of alumina and magnesia; and S: a content of unavoidable impure components which is 3% 25 or less by weight.

Preferably the refractory material of at least the interior surface of the nozzle and/or the portions that come into contact with molten steel are manufactured by using spinel raw materials.

Preferably the refractory material of at least the interior surface of the nozzle and/or the portions that come into contact with molten steel are composed of raw refractory material having a grain size of 1,000 jim or less and in which the ratio of grains of 500 jm or less is at least 60% by weight.

Preferably the thickness of the refractory material of at least the interior surface of the nozzle and/or the portions that come into contact with molten steel are 2 to mm.

Brief Description of the Drawings Fig. 1 shows an embodiment of a distribution pattern of materials in a nozzle of the present invention; Fig. 2 shows another embodiment of the distribution pattern of materials in the nozzle of the present invention; Fig. 3 shows another embodiment of the distribution pattern of materials in the nozzle of the present invention; Fig. 4 shows another embodiment of the distribution pattern of materials in the nozzle of the present invention; 1 Fig. 5 shows another embodiment of the distribution 20 pattern of materials in the nozzle of the present invention; and Fig. 6 shows a distribution pattern of materials in a conventional nozzle.

Embodiment An embodiment of the present invention will now be described in detail.

A nozzle for use in continuous casting of steel according to the present invention is characterized in that at least an interior surface of the nozzle and/or portions that come into contact with molten steel are composed of a refractory material comprising, as mineral phase, spinel or/and periclase.

00 The refractory material of the present invention does not contain carbon and SiO,. Accordingly, when the refractory material is used in the casting of aluminum killed steel, reactions according to the above-mentioned Equations to do not take place with the result that no network layer of A1 2 0 3 is formed on the working surface of the refractory material. As a result, adhesion of Al 2 0 3 inclusions onto the working surface and blockage of the nozzle due to the adhesion of the inclusions are remarkably suppressed.

so. Further, the refractory material of the present invention is a mineral phase comprising spinel, or spinel and periclase, and contains no free A1 2 0 3 Accordingly, when the refractory material is used for the casting of high oxygen content steel, high manganese content steel, and stainless steel, melt-damage of the refractory materials may be suppressed.

These particular reasons therefor may be described based on the experimental results in the following examples: A1 2 0 3 is present in the form of composite oxide (spinel) with MgO to thereby lower the thermodynamic activity of A1 2 0 3 with the result that MnO and FeO from molten steel can hardly penetrate to the refractory materials.

The reactivity between periclase and molten steel is small with the result that MnO and FeO from molten steel can hardly penetrate to periclase.

SThe solid-phase line temperature of MgO-spinel refractory materials exceeds 2,000°C, which is extremely high, with the result that even if MnO and FeO do penetrate, a liquid slag phase hardly occurs.

As described above, the feature of the nozzle of the present invention is to control the mineral composition of the refractory material to be used. In other words, even if the refractory material has a similar chemical composition, when the mineral compositions (crystal structure) are different from each other, the reactivity thereof with molten steel is naturally different, resulting in a large difference in the melt-damage of the refractory materials.

In the present invention, the refractory material of the interior surface of the nozzle and/or the portions that come into contact with molten steel are composed of spinel crystal, which is a composite oxide of A1 2 0 3 and MgO, or spinel crystal and periclase crystal consisting of MgO. However, when the refractory material of the present invention is prepared by using a practical refractory raw material, unavoidable impure minerals may exist therein, which may be accompanied by unavoidable impure components. It is preferable to suppress the unavoidable impure minerals as much as possible. Therefore, the content of impure components other than A1 2 0 3 and MgO, which are used for the formation of spinel and periclase, is preferably 3% or less by weight. If the content exceeds 3% by weight, the melt-damage resistance of the impure minerals that accompany the impure components is so low that the portions of the impure minerals is melt-damaged earlier than spinel and periclase, which is not preferable. More preferably, the content is 1% or less by weight.

The refractory material of the present invention used in the nozzles may be preferably applied to the interior surface and/or the portions that come into contact with molten steel of any nozzle used in continuous casting such as long nozzles or submerged nozzles.

With respect to manufacturing the nozzle, the nozzle may be manufactured by the following methods: A method (simultaneous molding method) may be used, in which the blend of the refractory raw material of the present invention that forms the interior surface and/or the portions to come into contact with molten steel and the blend of refractory raw material that forms the main body of the nozzle are simultaneously pressure molded to form a nozzle

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having a predetermined shape. Also, a method (finishing method) may be used, in which the blend mixed with the refractory raw material of the present invention composing the interior surface and/or the portions to come into contact with molten steel is cast-molded or pressure molded into the main body of a nozzle that has been preformed, then dried and occasionally sintered. In addition, A120 3 -C refractory material or A1 2 0 3 -SiO 2 -C refractory material, which has been conventionally used as refractory that forms the main body of the nozzle, may be appropriately used.

Examples of distribution patterns of the refractory materials in accordance with the present invention are given in Figs. 1 to 5. Here, Figs. 1 to 4 show the submerged nozzles with ZrO 2 -C refractory material arranged around a powder line. The powder line is a zone that comes into contact with a highly corrosive mold powder when the submerged nozzle is used. Accordingly, A1 2 0 3 -Sio 2 -C refractory material composing the main body of the nozzle has been replaced in this region by the Zr02-C refractory material which has superior corrosion resistance, to reinforce the powder line zone. Incidentally, the A1 2 0 3 -SiO0 2 -C refractory materials and Zr0 2 -C refractory materials of ordinary composition may be used, for instance, A1 2 0 3 -Si02-C refractory material composed of 30 to 90% by weight of A1 2 0 3 0 to 35% by weight of SiO 2 and to 35% by weight of C, or ZrO 2 -C refractory material composed of 66 to 88% by weight of ZrO 2 2 to 4% by weight of CaO, and 10 to by weight of C, for example, when CaO stabilized ZrO 2 is used.

Further, CaO stabilized ZrO 2 is widely used as the ZrO 2 raw material, but MgO stabilized Zr02, Y 2 0 3 stabilized ZrO 2 baddeleyite, etc., may also be used. In Figs. 1 to 5, reference numeral 1 denotes a refractory material comprising as mineral phase spinel or spinel and periclase, that is, the refractory material according to the present invention. It should be understood that the distribution patterns of materials in the nozzle of the present invention are not limited to those shown in Fig. 1 to Also, when manufacturing by simultaneous molding, the raw material blend of the refractory material such as A1 2 0-SiO 2

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refractory material composing the main body of the nozzle, which has been mixed with phenolic resin or polysaccharide as a binder, and the raw material blend of the refractory material according to the present invention composing the interior surface and/or the portions to come into contact with molten steel, may be filled into their given positions in the mold, formed by CIP, etc., and dried to obtain an unfired or fired product. The refractory material composing the main body of the nozzle and the refractory material according to the present invention composing the interior surface and/or the portions to come into contact with molten steel are preferably mixed with the same kind of binder.

When manufacturing by finishing, a starting material blend mixed with the same binder used in the main body of nozzle or a binder such as silicate, phosphate, etc., may be cast around the main body of a nozzle, which has been preformed by a conventional method, molded or pressure molded, then dried and occasionally fired.

However, it is not preferable to insert and load the interior portions (interior surface and/or portions to come into contact with molten steel), which have been made separately by pressure molding, cast molding or injection molding, into the main body, which has been conventionally preformed, because the interior portions do not easily stick to the refractory material composing the nozzle body. In particular, in order to maintain stable adhesion when heated at a high temperature in use, the above-mentioned simultaneous molding or finishing is preferable, because the refractory material according to the present invention composing the interior surface and/or the portions to come into contact with molten steel is composed of spinel, or spinel and periclase, so that it may have a greater expansion coefficient than that of the A1 2 0 3 -C or A1 2 0 3 -SiO 2 -C refractory material composing the main body of the nozzle.

Similarly, the refractory material composing the main body of the nozzle and the refractory material composing the interior surface and/or the portions to come into contact with molten steel are preferably mixed with the same kind of binder as described above to yield better affinity resulting in a stable adhesion.

On the other hand, in the manufacture of the refractory material according to the present invention, it is desirable to use as raw material a spinel raw material, or a spinel raw material and a magnesia raw material comprising periclase. When magnesia and alumina starting materials are used simultaneously as starting materials, magnesia reacts with alumina during the firing or use of the refractory materials to form spinel. However, the materials expand as the reaction progresses, and there is a risk that the materials may cracks. Incidentally, spinel raw materials, in which the ratio of MgO Al 3 composing spinel does not correspond to the theoretical composition and spinel and periclase coexist with an excess of MgO, or in which corundum crystals as free alumina are not found with an excess of A1 2 0 3 can be used. Both spinel and magnesia raw materials may be used irrespective of an electromolten or fired product.

The grain size of the starting materials blended to form the refractory material according to the present invention is preferably 1,000 gm or less, in which the ratio of grains having a grain size of 500 m or less is not less than 60% by weight. If particles having a grain size exceeding 1,000 gm are present, the grain size of the starting material in relation to the thickness of nozzle is too large, which will cause the refractory structure to become brittle, and will cause grains to fall out, etc., during use. Also, if the ratio of grains having a grain size of less than 500 gm or less is less than 60% by weight, the molding property is deteriorated, especially in simultaneous molding, and a satisfactory molded product can seldom be obtained. Incidentally, if the raw materials having a grain size of less than 0.5 lm exceeds by weight, the resistance to spolling of the refractory material is undesirably deteriorated, resulting in cracking.

Further, when the refractory material of the present invention is used for the interior surface of the nozzle and /or the portions that come into contact with molten steel, the thickness thereof is preferably with the range of 2 to 10 mm. Refractory material with a thickness of less than 2 mm, is weak and therefore not capable of withstanding the impact of the stream of molten steel, resulting in a risk that the nozzle will fall-out from the main body of the nozzle. Further, if the thickness exceeds 10 mm, the difference in thermal expansion coefficient with the refractory material composing the main body is large. Accordingly, there is a risk that cracking will result (deterioration of spolling resistance), which is not desirable.

Effect of the Invention Using the nozzle according to the present invention, blockage of the nozzle due to the adhesion of A1 2 03, inclusions during the casting of aluminum killed steel casting can be remarkably suppressed. Also, in the casting of high oxygen content steel, high

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manganese content steel stainless steel and Ca-treated steel, damage of the nozzles is remarkably reduced.

Example The tests of spalling resistance, A1 2 0 3 inclusions adhesion resistance and melt-damaged resistance performed on each of the samples in the examples and comparative examples below will now be explained.

In the spalling tests, samples 40 x 40 x 230 mm in dimension preheated at 800 0 C for one hour were immersed for 5 minutes in 1,580 0 C of molten steel that was prepared by dissolving 200 kg of steel in a high frequency furnace, and then pulled up to be cooled in air. Samples after cooling were evaluated on the basis of crack formation. Ten samples were prepared and were evaluated by the total number of samples in which cracks had formed.

In the melt-damage tests, samples of 40 mm in diameter and 230 mm in height were immersed in molten high oxygen content steel at 1,580 C in argon and rotated for 60 minutes at a speed of 100 rpm, then evaluated by the decrease in diameter of each sample.

In the A1 2 0 3 inclusions adhesion tests, samples of 40 mm in diameter and 230 mm in height were immersed in molten aluminum killed steel at 1, 580 0 °C in argon, rotated for 60 minutes at a speed of 100 rpm, then evaluated based on the thickness of A1 2 0, adhesion layer on the working surface of each sample.

Example 1 Two percent by weight (outer percentage) of phenol resin as binder were added to the starting material blends shown in Table 1 below, blended, CIP molded under a pressure of 1,000 kgf/cm 2 and then dried at 250 0 C for 3 hours to prepare samples. In this example, a spinel raw material having a nearly theoretical composition, in which the weight ratio of MgO Al 2 0 is 28 72, and a magnesia rich spinel raw material, in which the weight ratio of MgO A 2 0 3 is 50 were used.

The samples thus obtained were subjected to the spolling, melt-damage and Al 2 0 3 adhesion tests described above. The results obtained are given in Table 1.

16 Table 1 1 2 BLEND Magnesia 85 60 5-300,um) Magnesia 5 10 5,tm) Spinel of 3 theoretical composition -lOOO/t00,m) S pinel of 7 28 Theoretical Composition (O.5-500,um) Spinel of 2 Theoretical Composition MgO rich- Spinel (5OO-1000/tm) MgO rich- Spinel (O.5-500/Lm) MgO rich- spinel(<0.5/2m) Altumina- ChemLical Ma0 93 7-8 Composit A1 2 0, 7 22 ion Sio,

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Mineral Phase P.S P.S Test Spalling 0 0 Results resistance MRelt-damage 0 0 resistance A1 2 0 3 inclusions 0 0 Adhesion resistance INVENTIVE PRODUCT JCornparative Product 314 516 7 1 1~ IA 20 10 20 80 10 20 10 35 78 1.0 10 1 30 1 l10 14.6 65 22 50 50 35 65 28 60 40 50 50 1R 0 C10 90 78 22 3 41 2 28 3 1

C.M

0 a_ P. s 0 j j~ 0j 0 0 10 0 10 lot0-1 0 0 0 0 0 0 0 1 5 1 1 110 0 0 0 1 T0

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In Table 1, symbols in the row of 'Mineral Phase' indicate the following: P; periclase, S; spinel, C; corundum, and M; Mullite, respectively.

From the results shown in Table 1, the following can be ascertained:

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1) Comparative Product 1, which had a composition of 100% by weight of MgO, and Comparative Product 3, which had a composition of 78% by weight of MgO, 22% by weight of A1 2 0 3 and had periclase and corundum as mineral phase, had poor spalling resistance, but there were no such problems with any of the other samples.

2) Damage resistance was poorest in Comparative Product 4 (conventional A1 2 0 3 -SiO 2 -C refractory material), followed by Comparative Products 2 and 3, but there were no such problems with any of the other samples.

3) A1 2 0 3 inclusions adhesion was poor in Comparative Product 4, but A1 2 0 3 adhesion layer was not observed in any of the other samples.

Consequently, in the nozzle of the present invention, the refractory material disposed in the interior surface of the nozzle and/or the portions that come into contact with molten steel can be seen to simultaneously provide spalling resistance, damage resistance, and A1 2 0 3 inclusions adhesion resistance.

Example 2 The blend of starting material shown in Table 2 below was used to prepare samples by the same method as in Example 1, and spalling, damage, and A1 2 0, inclusions adhesion tests were performed.

The results obtained are given in Table 2.

BLEND Magnesia (>1000gm) Magnesia (0.5-300gm) Magnesia Spinel of Theoretical composition (>1000g/m) Spinel of Theoretical Composition (500-1000gm) Spinel of Theoretical Composition (0.5-500gm) Spinel of Theoretical Composition Chemical MgO Composition A1 2 0 3 (wt%) Mineral Phase Test Spalling resistance Results Melt-damage resistance A1 2 0 3 inclusions Adhesion resistance Table 2 INVENTIVE PRODUCT 8 9 10 11 65 60 60 52 5 10 10 18 f Comparative Product 5 6 50 54 10 16 2 10 5 15 23 14 18 28 20 15 5 2 2 5 6 78 22

P.S

0 0 0 78 78 22 22 P.S P.S 0 0 0 0 0 0 78 22

P.S

0 0 0 78 22

P.S

0 78 22

P.S

4 0 0 *The falling-out of coarse particles was detected.

From the results shown in Table 2, the following can be ascertained.

1) When the maximum grain size of the starting material exceeds 1,000 am, coarse particles fall out of the surface of the samples.

2) When the ratio of starting materials of less than um is not more than 20% by weight, the spalling resistance is barely affected, but when it exceeds 20% by weight, the spalling resistance lowers remarkably.

3) The particle size has little effect on the resistance to melt-damage and the adhesion of A1 2 0 3 inclusions.

Example 3 Using a main body of the nozzle composed of the A1 2 0 3 -SiO 2

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refractory material of Comparative Product 4 shown in Table 1 above, nozzles (external diameter of nozzle; 130 mm, internal diameter; mm, length; 600 mm) with the interior material of the nozzle of Inventive Product 1 shown in Table 1 above were prepared while varying the thickness of the interior materials (1 mm, 2 mm, 5 mm, 8 mm, 10 mm, and 12 mm, but the thickness of the main body of the nozzle was constant). The samples were simultaneously molded by CIP method, left for 24 hours, and then dried at 105°C for 24 hours.

The distribution pattern of the materials was as shown in Fig. The nozzle test samples thus obtained were immersed for 1 hour in 200 kg of molten steel, which was melted at 1,580 0 C in a high frequency furnace, and then compared for spalling resistance by crack formation. Ten test samples were prepared and the spalling resistance was evaluated by the number of test samples, in which cracks were formed. The test results are shown in Table 3.

Table 3 Inventive Product Comparative Product 12 13 14 15 7 8 Thickness of interior 2 5 8 10 1 12 material (mm) Spalling resistance 0 0 0 4 *The falling-out of interior material was detected.

From Table 3, it became clear that the interior material may be in danger of falling-out when the thickness of the interior surface is less than 2 mm, and that the spalling resistance deteriorates markedly when the thickness exceeds 10 mm.

Example 4 An actual machine test run was performed to evaluate the effect of the nozzle according to the present invention. The submerged nozzle of Inventive Product 13 shown in Table 3 as well as a conventional nozzle as comparison, which was made of the combination of A1 2 0 3 -SiO 2 -C refractory material of Comparative Product 4 of Table 1 and ZrO,-C refractory material (80% by weight of Cao stabilized ZrO 2 and 20% by weight of graphite) with a distribution pattern of materials shown in Fig. 6, were tested.

The tests were performed at a casting temperature of 1,580°C by using a low carbon aluminum killed steel (composition

C;

0.08, Si; 0.03, Mn; 0.2, P; 0.01, Al; 0.05, and 0; 10 ppm). After casting for 250 minutes, the thickness of the maximum Al 2 0 3 inclusions adhesion layer in the comparative nozzle was 15 mm, whereas it was only 3 mm in the nozzle of the present invention, showing a significant reduction effect in the A1 2 0 3 adhesion.

Further, there was no cracking and falling-out of the interior material of the nozzle, and safe operation could be carried out.

Example The test was performed by using two submerged nozzles similar to those in Example 4 for continuous casting of high oxygen content steel (composition C; 30 ppm, Si; 20 ppm, Mn; 0.3, P; 0.01, S; 0.01, Al; 10 ppm, and 0; 600 ppm). As a result of testing, the maximum thickness damaged of the interior pipe after casting for 230 minutes in the comparative nozzle was 11 mm, whereas it was only 1 mm in the nozzle of the present invention, showing a significant decrease in damage in the submerged nozzle. In this case, too, there was no cracking and falling-out of the interior material of the nozzle, and safe operation could be carried out.

Example 6 The test was performed by using two submerged nozzles similar to those in Example 4 for continuous casting of high manganese content steel (composition C; 0.04, Si; 0.02, Mn; 1.5, P; 0.01, S; 0.01, and 0; 100 ppm). As a result of testing, the maximum thickness damaged of the interior pipe after casting for 210 minutes in the comparative nozzle was 13 mm, whereas it was only 1.5 mm in the nozzle of the present invention, showing a significant decrease in damage in the submerged nozzle. In this case, too, there was no cracking and falling-out of the interior material of the nozzle, and safe operation could be carried out.

Example 7 The test was performed by using two submerged nozzles similar to those in Example 4 for continuous casting of stainless steel (composition C; 0.05, Si; 0.5, Mn; 1.0, P; 0.04, S; 0.02, Ni; 8.0, Cr; 18.0, and 0; 50 ppm). As a result of testing, the maximum thickness damaged of the interior pipe after casting for 260 minutes in the comparative nozzle was 9 mm, whereas it was only 0.5 mm in the nozzle of the present invention, showing a significant decrease in damage in the submerged nozzle. In this case, too, there was no cracking and falling-out of the interior material of the nozzle, and safe operation could be carried out.

Example 8 The test was performed by using two submerged nozzles similar to those in Example 4 for continuous casting of calcium treating steel (composition C; 0.05, Si; 0.3, Mn; 0.8, P; 0.01, S; 0.01, Al; 0.02, Ca; 30 ppm, and 0; 20 ppm). As a result of testing, the maximum thickness damaged of the interior pipe after casting for 200 minutes in the comparative nozzle was 8 mm, whereas it was only 1 mm in the nozzle of the present invention, showing a significant decrease in damage in the submerged nozzle. In this case, too, there was no cracking and falling-out of the interior material of the nozzle, and safe operation could be carried out.

Claims (4)

1. A nozzle for use in continuous casting of steel, characterized in that at least an interior surface of the nozzle and/or portions that come into contact with molten steel are of a refractory material consisting solely of a mineral phase of spinel, or spinel and periclase; a constituent element which is substantially composed of alumina and magnesia; and a content of unavoidable impure components which is 3% or less by weight.

2. A nozzle for use in continuous casting of steel according to claim 1, wherein the refractory material is manufactured by using spinel raw materials.

3. A nozzle for use in continuous casting of steel according to claim 1 or 2, wherein the refractory material oo*: is composed of a raw refractory material having a grain .T 20 size of 1,000 itm or less and in which the ratio of grains of 500 atm or less is at least 60% by weight.

4. A nozzle for use in continuous casting of steel according to any one of claims 1 to 3, wherein the 25 thickness of the refractory material of at least the *"t interior surface of the nozzle and/or the portions to come into contact with molten steel is 2 to 10 mm. A nozzle for use in continuous casting of steel substantially as herein described with reference to the accompanying drawings, except for Figure 6.