T 1067/00 26-06-2003

Reasons for the Decision

1. The appeal is admissible.

2. Given that essentially claim 3 was objected to in the appealed decision, the following arguments pertain to claim 3 in particular of set C (second auxiliary request). The reason for this is that this claim represents the most preferred embodiment of the claimed process and, therefore, the same arguments apply equally to claim 3 of the main and first auxiliary request and to claim 1 of the third auxiliary request which are all broader in scope.

3. Novelty

Although the novelty of the claimed process was questioned by the examining division, the Board holds the view that document D1 does not disclose clearly and unambiguously the technical feature which is stipulated in all independent claims of the present application that, after forging the ingot in its (original) width direction, a new width direction and a new thickness direction is necessarily formed.

4. Inventive step

4.1. Technical background; the closest prior art

Like the present application, document D1 relates to "thick" plates from AA 7000 series Al alloys ranging from 3 to 10 inches in thickness (cf. D1, column 2, lines 45 to 53; column 5, lines 11 to 16). Such plates are used for the manufacture of aircraft structural members and, therefore, their fatigue properties and other long time mechanical properties have to be eminent. As compared to the fatigue properties of "thin" Al plates, document D1 observes in column 1, lines 13 to 16 that owing to porosity the logarithmic average fatigue life of "thick" Al-plates decreases the more thickness increases. Such porosity is due to micropores which develop during solidification of the molten metal either when gaseous components, in particular hydrogen, dissolved in the melt are released thus generating microvoids and holes in the cast ingot, or when the ingot "shrinks". (cf. D3, column 2, line 53 to column 3, line 3).

To cope with the problem of microporosity and, in consequence thereof, to maximize the fatigue properties of "thick" (i.e. 3 to 10 inches) Al plate products without adversely affecting other mechanical properties such as tensile strength, toughness and ductility, document D1, therefore, advocates a method comprising, in addition to a degassing of the melt, a pre-working operation which is effective to reduce the microporosity prior to rolling or working (cf. D1, column 1, lines 19 to 22; column 2, line 65 to column 4, line 49). The fatigue lifetime of the Al- plate is determined under cyclic loading pursuant to the ASTM test method E-466 (cf. D1, column 1, lines 65 to column 2, line 2; column 5, lines 61 to 64). The object and the test method described in document D1 and the present application being the same, this document is considered to represent the closest prior art.

However, document D1 does not disclose a double rolling operation and is silent about a minimum fracture toughness KIC(T-L) as does claim 3 of set C (second auxiliary request).

4.2. Technical problem and solution

The object of the present application, therefore, resides in providing a process which results in "thick" Al alloy plate products exhibiting fatigue properties and mechanical properties superior to those obtained in products produced by the prior art process proposed in document D1.

This object is achieved (i) by a forging step in the width direction of the ingot so that a "new" width is formed and (ii) by hot rolling the billet in the new width and length direction. These steps, however, are obvious to a person skilled in the art as is shown in the following.

4.2.1. Although the application does not specifically address the phenomenon of microporosity and the problems associated therewith, the skilled person is completely aware of the fact that a low degree of microporosity is the key prerequisite for a high fatigue resistance in the final Al alloy plate. This is evident from document D1 alone. This background knowledge has also been corroborated by the applicant during the oral proceedings and by the post- published documents D2 and 3 enclosed with the applicant's grounds of appeal. In this context reference is made for instance to document D2, page 2, column 3. To decrease the microvoid fraction or close the micropores, D1 proposes - prior to hot rolling - an effective forging operation wherein the ingots are preferably deformed (forged or squeezed) in the thickness direction (C-direction) by 5 to 80% reduction of their original thickness. However, document D1 further teaches as an alternative that the ingot may also be deformed either in the width direction (B-direction) after a C-direction deformation, or in the width direction alone so that a billet forged to an intermediate thickness and/or width dimension is obtained (cf. D1, column 3, lines 55 to 62; column 4, lines 47 to 49). The latter operation essentially corresponds to the forging step stipulated in the claimed process. Although document D1 does not expressly mention that after heavy forging a "new" width and a "new" thickness direction of the ingot needs to be formed and further hot rolling in this new width and length direction has to be performed, such operations are carried out without inventive efforts by a skilled metallurgist who is familiar with forging and rolling. When executing the basic teaching given in document D1, the skilled metallurgist will choose the reduction rate sufficiently high to minimize or even eliminate the microporosity of the plate.

4.2.2. As regards the double hot rolling step in the width and length direction, it is evident from the application (see example 4) that already hot rolling in the length direction alone suffices to achieve the desired fatigue strength and level of the mechanical properties. The appellant referred to the supplementary test results showing that by rolling in the width and length direction the L-T and T-L fracture toughness are almost equal so that the Al-plate product shows almost isotropy in the mechanical properties.

It is, however, basic metallurgical knowledge that the grain growth orientation is influenced by the rolling direction, thus resulting in an anisotropy of the mechanical properties which can be avoided by rolling in different directions. Therefore, the claimed hot rolling the ingot in the "new" width and the length direction, is only this usual measure to avoid anisotropy of the properties in the final product.

4.2.3. At the oral proceedings, the applicant conceded that an overlap exists between the process described by D1 and that claimed as regards the pre-forging steps to deform the ingot. Referring to decisions T 26/85 and T 751/94, the applicant argued that the skilled person would, in the light of the technical facts disclosed in D1, not have seriously contemplated applying the technical teaching of the prior art in the range of overlap.

This argument is, however, not convincing for the following reasons. Although all the claims in document D1 relate to a pre-forging in the thickness direction (C-direction) which is specified as being the most preferred direction, document D1 nevertheless recommends alternative pre-forging steps either in the width and thickness direction or in the width direction alone. Document D1 does not provide any prejudice or warning prompting the reader skilled in the art to exclude a pre-forging step in the width direction alone and at a reduction rate of more than 50% in this direction so that a "new" width and thickness direction is obtained. Hence there is no reason to disregard this part of technical information included in document D1.

4.2.4. Process claim 3 further stipulates that, dependent upon the plate thickness, a minimum value for the fracture toughness is to be obtained by the claimed method.

The Board acknowledges that - in addition to an increased resistance to fatigue - an improvement in fracture toughness of the Al-plates could be obtained by the claimed process. It is, however, considered that the desired toughness properties stipulated by the formula in claim 3 are nearly achieved also by the Al- plate given in document D1. For the 5.7-inch thick plate (example given in D1), the KIC(L-T) minimum value according to the claimed formula is calculated to be 24.36. Ksi square root of inch. This value is rather close to the fracture toughness of 24.0 Ksi square root of inch which is obtained by the process disclosed in document D1 (cf. D1, column 6, line 17).

4.2.5. In summary the claimed process therefore represents a mere optimisation of the pre-forging and rolling operations already known from document D1 so that in particular the fatigue strength and - as a bonus effect - the fracture toughness of the resulting "thick" Al-plate are further improved. The mere optimisation of an existing technology does, however, not involve an inventive step.

4.3. Since the same reasoning is valid for the process claimed in claim 3 either of the main and the first auxiliary request or that claimed in claim 1 of the third auxiliary request, the claims of these requests are equally not allowable for lack of inventive step of the claimed subject matter.