Process for treating a titanium alloy or article made therefrom

Abstract: A process for treating a titanium alloy comprising subjecting said alloy to a solution treatment, quenching the solution treated alloy, and ageing the quenched alloy below the β transformation point characterised in that the titanium alloy is an α + β titanium alloy or a β titanium alloy which is subjected to a β solution treatment above the β transformation point. Alloys produced by this method can be highly polished to a mirror-like finish.

Description: The present invention relates to a process for treating an α + β titanium alloy article or a β titanium alloy article. In general an α + β titanium alloy article is a two phase alloy comprising a hard phase and a soft phase and there is a difference in the hardness and the workability between the α phase and the β phase. Therefore, even when such an attempt is made to subject such an article to a mirror finishing, a mirror state cannot be produced. Moreover, in the case of a β titanium alloy article as well, an α phase is present although the amount thereof is small, and thus makes it impossible to produce a mirror state due to a difference in the hardness and the workability between the α phase and the β phase. A process of solution treating, quenching and ageing α + β or β titanium alloys is known from Titanium: A Technical Guide (1988), Ed. M.J. Donachie, Jr. at pages 27 and 62-68. Additionally said document discloses on page 98 the polishing and buffing of titanium alloys. A heat treatment of a titanium alloy article, which has been conducted for the purpose of enhancing the strength or toughness of the article, is disclosed in Japanese Patent Publication No. 48025/1983 and Japanese Patent Laid-Open No. 281860/1986. In this heat treatment, the article is solution treated below the β transformation point, is quenched, and is aged below the β transformation point. In such a treatment, a pro-eutectoid α phase remains and there is a difference in the hardness and the workability between the pro-eutectoid α phase and the phase precipitated from the β phase by the ageing treatment, so that a mirror state cannot be obtained even if an attempt to produce mirror finishing is carried out. Therefore, a titanium alloy article has been given a satin finish state or has been given a surface treatment such as overcoating. A titanium alloy has many advantages such as high specific strength, high temperature strength and good corrosion resistance and has therefore been extensively used for constructional or mechanical parts. In such products, a heat treatment is carried out for the purpose of imparting various functions such as strength, toughness, corrosion resistance and vibration resistance. The appearance of the product has not been of importance and a mirror state has not been considered necessary. In recent years, however, these products have been used for ornaments by virtue of features of the titanium alloy such as low specific gravity, good corrosion resistance, high hardness and high-grade finish. In this case, these products have been used after a surface treatment such as overcoating or in a satin finish pattern, but it has not been possible to give them a mirror state. The reason for this is as follows. In a titanium alloy, there is both a hard phase 2 and a soft phase 1 (as shown in Figure 1(A)), so that, in the mirror finishing treatment, the soft phase 1 is selectively polished (as shown in Fig.1(B)), or otherwise the soft phase 1 is broken away (as shown in Figure 1(C)). This causes an uneven portion to be formed on the finished surface, so that a satin finish pattern is formed and a mirror state cannot be produced. According, therefore, to the present invention, there is provided a process for treating an α + β titanium alloy article or a β titanium alloy article comprising subjecting said alloy article to a β solution treatment above the β transformation point, quenching the solution treated alloy article, and ageing the quenched alloy below the β transformation point characterised in that the alloy is moulded into an article having a desired final shape prior to the said solution treatment, and said article is finally subjected to a mirror finishing treatment. Thus the finishing treatment is preferably a polishing treatment. Preferably, after the said ageing, the article is gradually cooled to room temperature. The said quenching preferably produces a martensitic phase (e.g. a martensitic single phase) or a β phase (e.g. a β single phase). The said ageing may produce the fine precipitation of an α phase or an ω phase in a martensitic phase matrix or a β phase matrix. The said quenching may cause α and ω phases to be homogeneously and finely precipitated. The process of the present invention enables titanium alloy ornaments to be produced without detriment to their high hardness and without marring the resistance characteristics of the titanium alloy even though mirror finishing is used as a post-treatment. The invention is illustrated, merely by way of example, in the accompanying drawings, in which:- Figure 1(A) is a cross-sectional view of a known titanium alloy article before mirror finishing; Figures 1(B) and (C) are cross-sectional views of a known titanium alloy article after mirror finishing; Figure 2(A) is a photomicrograph (x 400) showing the structure of a Ti-9.5V-2.5Mo-3Aℓ alloy before a heat treatment; Figure 2(B) is a photomicrograph (x 400) showing the structure of a Ti-9.5V-2.5Mo-3Aℓ alloy after a solution treatment (at 750°C for 0.5 h) followed by oil cooling; Figure 2(C) is a photomicrograph (x 400) showing the structure of a Ti-9.5V-2.5Mo-3Aℓ alloy after a solution treatment (at 750° C for 0.5 h) followed by oil quenching and an ageing treatment (at 500°C for 5 h); Figure 2(D) is a photomicrograph (x 400) showing the structure of a Ti-9.5V-2.5Mo-3Aℓ alloy after a solution treatment (at 850°C for 0.5 h) followed by oil quenching; Figure 2(E) is a photomicrograph (x 400) showing the structure of a Ti-9.5V-2.5Mo-3Aℓ alloy after a solution treatment (at 850°C for 0.5 h) followed by oil quenching and an ageing treatment (at 400°C for 16 h); Figure 2(F) is a photomicrograph (x 400) showing the structure of a Ti-9.5V-2.5Mo-3Aℓ alloy after a solution treatment (at 850°C for 0.5 h) and an ageing treatment (at 450°C for 16 hr); Figure 2(G) is a photomicrograph (x 400) showing the structure of Ti-9.5V-2.5Mo-3Aℓ alloy after a solution treatment (at 850°C for 0.5 h) and an ageing treatment (at 500°C for 16 h); Figure 3 is a graph showing the Vickers hardness of a Ti-99.5V-2.5Mo-3Aℓ alloy after a solution treatment (at 850°C for 0.5 h) followed by oil quenching and an ageing treatment; Figure 4 is a graph showing the Vickers hardness of a Ti-9.5V-2.5Mo-3Aℓ alloy after a solution treatment (at 750°C for 0.5 h) followed by oil quenching and an ageing treatment; Figure 5(A) is a photomicrograph (x 400) showing the structure of a Ti-6Aℓ-4V alloy before a heat treatment; Figure 5(B) is a photomicrograph (x 400) showing the structure of a Ti-6Aℓ-4V alloy after a solution treatment (at 900°C for 0.5 h) followed by oil quenching; Figure 5(C) is a photomicrograph (x 400) showing the structure of a Ti-6Aℓ-4V alloy after a solution treatment (at 900°C for 0.5 h) followed by oil quenching and an ageing treatment at (600° for 5 h); Figure 5(D) is a photomicrograph (x 400) showing the structure of a Ti-6Aℓ-4V alloy after a solution treatment (at 1050°C for 0.5 h) followed by oil quenching; Figure 5(E) is a photomicrograph (x 400) showing the structure of a Ti-6Aℓ-4V alloy after a solution treatment (at 1050°C for 0.5 h) followed by oil quenching and an ageing treatment (at 400°C for 16 h); Figure 5(F) is a photomicrograph (x 400) showing the structure of a Ti-6Aℓ-4V alloy after a solution treatment (at 1050°C for 0.5 h) followed by oil quenching and an ageing treatment (at 500°C for 16 h); Figure 5(G) is a photomicrograph (x 400) showing the structure of a Ti-6Aℓ-4V alloy after a solution treatment (at 1050°C for 0.5 h) followed by oil quenching and an ageing treatment (at 600°C for 16 h); Figure 5(H) is a photomicrograph (x 400) showing the structure of a Ti-6Aℓ-4V alloy after a solution treatment (at 1050°C for 0.5 h) followed by oil quenching and an ageing treatment (at 600°C for 16 h); Figure 6 is a graph showing the Vickers hardness of a Ti-6Aℓ-4V alloy after a solution treatment (at 1050°C for 0.5 h) followed by oil quenching and an ageing treatment; Figure 7 is a graph showing the Vickers hardness of a Ti-6Aℓ-4V alloy after a solution treatment (at 900°C for 0.5 h) followed by oil quenching and an ageing treatment; Figure 8(A) is a photomicrograph (x 400) showing the structure of a Ti-15V-3Aℓ-3Sn-3Cr alloy before a heat treatment; Figure 8(B) is a photomicrograph (x 400) showing the structure of Ti-15V-3Aℓ-3Sn-3Cr alloy after a solution treatment (at 750°C for 10 min) followed by oil quenching; Figure 8(C) is a photomicrograph (x 400) showing the structure of a Ti-15V-3Aℓ-3Sn-3Cr alloy after a solution treatment (at 750°C for 10 min) followed by oil quenching and an ageing treatment (at 450°C for 40 h); Figure 8(D) is a photomicrograph (x 400) showing the structure of a Ti-15V-3Aℓ-3Sn-3Cr alloy after a solution treatment (at 700°C for 10 min) followed by oil quenching; Figure 8(E) is a photomicrograph (x 400) showing the structure of a Ti-15V-3Aℓ-3Sn-3Cr alloy after a solution treatment (at 700°C for 10 min) followed by oil quenching and an ageing treatment (at 450°C for 40 h); and Figure 9 is a graph showing the Vickers hardness of a Ti-15V-3Aℓ-3Sn-3Cr alloy after a solution treatment (at 700°C for 10 min) followed by oil quenching and an ageing treatment. The preferred process of the present invention comprises subjecting an α + β titanium alloy or a β titanium alloy to a β solution treatment above the β transformation point, quenching the treated alloy to room temperature, and subjecting the quenched alloy to an ageing treatment below the β transformation point to precipitate a fine precipitate from the martensitic phase and the β phase on the whole surface. The structure of an α + β titanium alloy is converted into a martensitic single phase when the alloy is heated and held above the β transformation point (β solution treatment) and then quenched. On the other hand, the structure of a β titanium alloy is converted into a β single phase when the alloy is heated and held above the β transformation point and then quenched. Further, when the alloy is aged below the β transformation point, a fine precipitate of an α phase or an ω phase is formed in a martensitic phase matrix or β phase matrix. When the alloy is polished for mirror finishing in such a structure so that an α phase or an ω phase is precipitated in a martensitic phase, or an α phase or an ω phase is precipitated in a β phase, the surface of the titanium alloy can be uniformly polished and a mirror state can be provided. The present invention will now be described in more detail with reference to the accompanying drawings. Example 1 In the present Example, use was made of an α + β (near β) titanium alloy. Ingredient Ti Al Mo V wt% balance 3 2.5 9.5 The structure of the above-mentioned titanium alloy, when subjected to various heat treatments, is shown in Figure 2. Figure 2(A) shows the structure of the titanium alloy of Table 1 before a heat treatment, wherein two phases, i.e. α and β phases, are present in the structure. Figure 2(B) shows the structure of the titanium alloy of Table 1 after a solution treatment at 750°C for 0.5 h followed by oil quenching, wherein two phases, i.e. α and β phases are present in the structure. Figure 2(C) shows the structure of the titanium alloy of Table 1 after a solution treatment at 750°C for 0.5 h followed by oil quenching and an ageing treatment at 500°C for 5 h, wherein a fine α phase is precipitated from a β phase and a pro-eutectoid α phase remains as it is. Figure 2(D) shows the structure of the titanium alloy of Table 1 after a solution treatment at 850°C for 0.5 h followed by oil quenching, wherein the structure is a martensitic one. Figure 2(E) shows the structure of the titanium alloy of Table 1 after a solution treatment at 850°C for 0.5 h followed by oil quenching, and an ageing treatment at 400°C for 0.5 h and air cooling, wherein a fine ω phase is precipitated from a martensitic matrix. Figure 2(F) shows the structure of the titanium alloy of Table 1 after a solution treatment at 850°C for 0.5 h followed by oil quenching, and an ageing treatment at 400°C for 16 h and air cooling, wherein a fine α phase or ω phase is precipitated from a martensitic matrix. Figure 2(G) shows the structure of the titanium alloy of Table 1 after a solution treatment at 850°C for 0.5 h followed by oil quenching, and an ageing treatment at 500°C for 16 h and air cooling, wherein a fine acicular α phase is precipitated from a martensitic matrix. Thus, in the titanium alloy of Table 1, a martensitic single phase structure having no α phase remaining therein was prepared through a solution treatment above the β transformation point (780°C) followed by oil quenching. In this case, a period of 5 min or longer was necessary for the solution treatment. An ageing treatment in this state below the β transformation point gave rise to a structure wherein a fine ω phase was precipitated from a martensitic matrix when the temperature was below 450°C, and a structure wherein a fine α phase was precipitated from a martensitic matrix when the temperature was above 450°C. On the other hand, when the alloy was solution treated below the β transformation point and then oil quenched, a two-phase structure of α and β phases was formed. A further ageing treatment below the β transformation point brought about the formation of the structure so that a fine α phase was precipitated from the β phase and a pro-eutectoid α phase remained in the structure. Figures 3 and 4 show the hardness of the titanium alloy when subjected to various heat treatments. Figure 3 is a graph showing the hardness of the titanium alloy of Table 1 after a solution treatment at 850°C for 0.5 h followed by quenching and an ageing treatment. The titanium alloy of Table 1, when subjected only to a solution treatment, exhibited a Vickers hardness, Hv, of 260. In each ageing treatment temperature, the Hv value was above 350 when the ageing tretment time was 2h, i.e. the effect of the ageing treatment was obtained. This effect could be attained by virtue of the precipitation of a fine α phase or ω phase from the martensitic matrix. Figure 4 is a graph showing the hardness of the titanium alloy of Table 1 after a solution treatment at 750°C for 0.5 h followed by quenching and an ageing treatment. The titanium alloy of Table 1, when subjected only to a solution treatment, exhibited a Vickers hardness, Hv, of 240. When this alloy was aged, the Hv value reached 420 when the ageing treatment was conducted at 400°C for 5 h, and reached 370 when the ageing treatment was conducted at 500°C for 5 h. This suggests that the effect of hardening by precipitation of an α phase or an ω phase from the α + β phase was attained. The results of a mirror finishing treatment of the titanium alloy of Table 1, which has been subjected to various heat treatments, are shown in Table 3. Table 3 shows a specific roughness and surface state after polishing. The surface roughness was represented in terms of the maximum value, the minimum value, and the average value of the maximum surface roughness, Rmax, when measurements were conducted at seven points at intervals of 2 mm for each sample. The titanium alloy of Table 1, when subjected to a solution treatment at 750°C for 0.5 h followed by an ageing treatment at 500°C for 5 h, exhibited an Hv value of 370 and had only small corrugation and surface roughness but could be given only an uneven polishing due to the difference in the hardness between the α phase and the β phase, so that a satin finish pattern was formed. On the other hand, the titanium alloy of Table 1, when subjected to a solution treatment of 850°C for 0.5 h followed by oil quenching and an ageing treatment at 450°C for 5 h or at 500°C for 5 h, exhibited a high Vickers hardness and a small surface roughness, comprised an α phase or an ω phase uniformly and finely precipitated in a martensitic matrix, was free from the risk of having uneven polishing, and could be given a mirror state. The titanium alloy of Table 1, when aged at 400°C for 5 h, brought about no complete precipitation of an α phase or a ω phase, so that slight uneven polishing was observed. Thus, in the α + β titanium alloy, an excellent mirror state could be attained by solution-treating the alloy above the β transformation point, quenching the treated alloy, ageing the alloy below the β transformation point to form a structure wherein a fine α phase or ω phase was precipitated from a martensitic matrix, and subjecting the alloy to a mirror finishing treatment. Example 2 In the present Example, various heat treatments specified in Table 5 were carried out on the α + β titanium alloy listed in Table 4. Ingredient Ti Aℓ V wt% balance 6 4 The structures of the titanium alloy of Table 4 subjected to various heat treatments are given in Table 5. Figure 5(A) shows the structure of the titanium alloy of Table 4 before heat treatment, wherein the structure comprises two phases, i.e. α and β phases. Figure 5(B) shows the structure of the titanium alloy of Table 4 after a solution treatment at 900°C for 0.5 h followed by oil quenching, wherein the structure comprises two phases, i.e. α and β phases. Figure 5(D) shows the structure of the titanium alloy of Table 4 after a solution treatment at 1050°C for 0.5 h followed by oil quenching, wherein the structure is a martensitic one. Figure 5(E) shows the structure of the titanium alloy of Table 4 after a solution treatment of 1050°C for 0.5 h followed by oil quenching, an ageing treatment at 400°C for 16 h and air cooling, wherein a fine ω phase is precipitated in a martensitic matrix. Figure 5(F) to (H) each show the structure of the titanium alloy of Table 4 after a solution treatment at 1050°C for 0.5 h followed by ageing treatment at 500°C for 16 h, at 600°C for 16 h and at 700°C for 16 h and air cooling, wherein a fine α phase is precipitated from a martensitic matrix. Thus, the structure of the titanium alloy of Table 4 was converted into a martensitic single phase structure by solution-treating the alloy above the β transformation point (995°C) followed by cooling at a rate higher than that attained by oil quenching. A further ageing treatment in this state below the β transformation point gave rise to a structure wherein a fine ω phase was precipitated from a martensitic matrix (ageing treatment temperature: 400°C) or a structure wherein a fine α phase was precipitated from a martensitic matrix (ageing treatment temperature: 400°C). A solution treatment below the β transformation point followed by oil quenching brought about a two-phase structure of α and β phases, and a further ageing treatment below the β transformation point gave rise to a structure wherein a fine α phase or ω phase was precipitated from a β phase and a pro-eutectoid α phase remained in the structure. The hardnesses of the titanium alloy of Table 4, when subjected to various heat treatments, are given in Figures 6 and 7. The alloy of Table 4, when subjected to a solution treatment at 1050°C for 0.5 h followed by oil quenching, exhibited a Vickers hardness, Hv, of 335. A further ageing treatment below the β transformation point improved the Hv value from 350 to 370. This effect derives from the formation of a structure wherein a fine α phase or ω phase is precipitated from a martensitic matrix. On the other hand, the titanium alloy of Table 4, when subjected to a solution treatment at 900°C for 0.5 h followed by oil quenching, exhibited a Hv value of 350. In this case, even when the alloy was further subjected to an ageing treatment at 600°C for 5 h, the Hv value was still 345. In other words, although a fine α phase was precipitated in a β phase, no improvement in the hardness was attained because the amount of the β phase was small. The results of a mirror finishing treatment of the titanium alloy of Table 4, when subjected to various heat treatments, are given in Table 6. Solution treatment 1050°C, 0.5 h (O.Q.) 900°C, 0.5 h (O.Q.) Aging treatment - 400°C 16 h 500°C 16 h 600°C 16 h 700°C 16 h - 600°C 5 h Surface roughess max. Rmax (µm) 0.804 0.531 0.329 0.199 0.163 0.649 0.415 min. Rmax (µm) 0.161 0.083 0.110 0.095 0.091 0.331 0.237 average (µm) 0.521 0.261 0.200 0.136 0.132 0.412 0.299 Surface state satin slightly satin good good good slightly satin satin Note: *: The mirror finishing was conducted by polishing with a sand paper, then with an abrasive and finally with a buff. As is apparent from Table 6, the titanium alloy of Table 4, when subjected to a solution treatment at 900°C for 0.5 h followed by oil quenching, and the titanium alloy of Table 4, when subjected to a further ageing treatment at 600°C for 5 h, provided no mirror state even when a mirror finishing treatment was carried out. By contrast, the titanium alloy of Table 4, when subjected to a solution treatment at 1050°C for 0.5 h followed by oil quenching and an ageing treatment at 500°C for 16 h, at 600°C for 16 h and at 700°C for 16 h provided an excellent mirror state as a result of a mirror finishing treatment. However, when the ageing treatment was conducted at 400°C for 16 h, an α phase or ω phase was not completely precipitated, so that no mirror state could be obtained. As is apparent from the foregoing description in the α + β titanium alloy, an excellent mirror state can be provided by solution-treating the alloy above the β transformation point, quenching the alloy to room temperature, ageing the quenched alloy below the β transformation point to form a structure wherein a fine α phase or ω phase is precipitated in a martensitic matrix, and subjecting the aged alloy to a mirror finishing treatment. Example 3 In the present Example, various heat treatments specified in Table 8 were carried out on the β titanium alloy listed in Table 7. Ingredient Ti V Aℓ Sn Cr wt% balance 15 3 3 3 The structures of the titanium alloy of Table 7, when subjected to various heat treatments, are shown in Figure 8. Figure 8 (A) shows the structure of the titanium alloy of Table 7 before a heat treatment, wherein there is a long thin β grain boundary. Figure 8(B) shows the structure of the titanium alloy of Table 7 after a solution treatment at 750°C for 10 min. followed by oil quenching, wherein the structure is an isometric β single phase structure. Figure 8(C) shows the structure of the titanium alloy of Table 7 after a solution treatment at 750°C for 10 min. followed by oil quenching and an ageing treatment at 450°C for 40 h, wherein a fine α phase. is precipitated from the whole β phase. Figure 8(D) shows the structure of the titanium alloy of Table 7 after a solution treatment at 700°C for 10 min followed by oil quenching, wherein a β phase is contaminated with an α phase. Figure 8(E) shows the structure of the titanium alloy of Table 7 after a solution treatment at 700°C for 10 min followed by oil quenching and an ageing treatment at 450°C for 40 h, wherein a pro-eutectoid α phase remains in the structure although a fine α phase is precipitated from a β phase. Thus, in the titanium alloy of Table 7, a structure wherein a fine α or ω phase is precipitated from a β phase is prepared by solution-treating the alloy above the β transformation point (730°C) and cooling the treated alloy to room temperature at a rate higher than that attained by oil quenching to form a β single phase structure and then ageing the alloy below the β transformation point. The hardness of the titanium alloy of Table 7, when subjected to various heat treatments, are given in Figure 9. As is apparent from Figure 9, the alloy of Table 7, when subjected to a solution treatment at 750°C for 10 min followed by oil quenching, exhibited a Vickers hardness, Hv, of 260, and an ageing treatment below 600°C provided a Hv value of above 300. The effect of the ageing treatment could be attained when the ageing time was above 40 h. This is because a fine α phase or ω phase is precipitated from the β phase. The results of a mirror finishing treatment of the titanium alloy of Table 7, when subjected to various heat treatments, are given in Table 9. Solution treatment 750°C, 0.5 h (O.Q.) 700°C, 0.5 h (O.Q.) Aging treatment - 500°C 40 h - 450°C 40 h Surface roughness max. Rmax (µm) 1.897 0.212 0.470 0.473 min. Rmax (µm) 0.525 0.075 0.279 0.256 average (µm) 1.029 0.151 0.380 0.392 Surface state satin good satin satin Note: *: The mirror finishing was conducted by polishing with a sand paper, then with an abrasive and finally with a buff. As is apparent from Table 9, the titanium alloy of Table 7, when subjected to a solution treatment at 750°C for 10 min followed by oil quenching and an ageing treatment at 450°C for 40 h, provided an excellent mirror state as a result of a mirror finishing treatment. As is apparent from the foregoing description, in a β titanium alloy, an excellent mirror state can be attained by solution-treating the alloy above the β transformation point, quenching the treated alloy to room temperature, ageing the alloy below the β transformation point to form a structure wherein a fine α phase or an ω phase is precipitated from a β phase, and subjecting the aged alloy to a mirror finishing treatment. As is apparent from the foregoing description, a structure wherein a fine α phase or an ω phase is uniformly precipitated from a martensitic single phase or a β single phase can be formed by heat-treating an α + β titanium alloy or a β titanium alloy, and an excellent mirror state can be attained by a mirror finishing treatment of such a structure. This makes it possible to provide ornaments having a high-grade finish due to an imparted mirror surface effect without detriment to the high hardness and without marring the resistance characteristics of the titanium alloy.

Claims: A process for treating an α + β titanium alloy article or a β titanium alloy article comprising subjecting said alloy article to a β solution treatment above the β transformation point, quenching the solution treated alloy article, and ageing the quenched alloy below the β transformation point characterised in that the alloy is moulded into an article having a desired final shape prior to the said solution treatment, and said article is finally subjected to a mirror finishing treatment. A process as claimed in claim 1 characterised in that, after the said ageing, the article is gradually cooled to room temperature. A process as claimed in claim 1 in which the mirror finishing treatment is a polishing treatment. A process as claimed in any preceding claim characterised in that the said quenching produces a martensitic phase or a β phase. A process as claimed in claim 4 characterised in that the said quenching produces a martensitic single phase or a β single phase. A process as claimed in any preceding claim characterised in that the said ageing produces the fine precipitation of an α phase or an ω phase in a martensitic phase matrix or a β phase matrix. A process as claimed in claim 4 or 5 characterised in that the said quenching causes α and ω phases to be homogeneously and finely precipitated.

Inventors: ABE AKIHIKO C O SEIKO INSTRUME, KATO KENZO C O SEIKO INSTRUMEN, MIYAMA SHIGERU C O SEIKO INSTR, WAKABAYASHI YUTAKA C O SEIKO I, ABE, AKIHIKO, C/O SEIKO INSTRUMENTS INC., KATO, KENZO, C/O SEIKO INSTRUMENTS INC., MIYAMA, SHIGERU, C/O SEIKO INSTRUMENTS INC., WAKABAYASHI, YUTAKA, C/O SEIKO INSTRUMENTS INC.
Applicants: SEIKO INSTR INC, SEIKO INSTRUMENTS INC.
Application year: 1990
Main classification: C22F1
IPC codes: C22F1