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(11) | EP 0 105 368 B1 |
| (12) | EUROPEAN PATENT SPECIFICATION |
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METHOD OF HOT-FORMING METALS PRONE TO CRACK DURING ROLLING VERFAHREN ZUR WARMVERFORMUNG VON METALLEN, DIE BEIM WALZEN RISSANFÄLLIG SIND PROCEDE DE FORMAGE A CHAUD DE METAUX SUSCEPTIBLES DE SE FISSURER PENDANT LE LAMINAGE |
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| Note: Within nine months from the publication of the mention of the grant of the European patent, any person may give notice to the European Patent Office of opposition to the European patent granted. Notice of opposition shall be filed in a written reasoned statement. It shall not be deemed to have been filed until the opposition fee has been paid. (Art. 99(1) European Patent Convention). |
Technical Field
[0001] The present invention relates to the hot forming of metals, and more particularly relates to the continuous casting and hot forming of the as-cast bars of certain impure or alloyed steels which may be prone to crack during hot-rolling.
Background Art
[0002] It is well known that metals, such as copper and aluminum, may be continuously cast, either in stationary vertical molds or in a rotating casting wheel, to obtain a cast bar which is then immediately hot formed, while in a substantially as-cast condition, by passing the cast bar exiting the mold to and through the roll stands of a rolling mill while the cast bar is still at a hot-forming temperature. It is also well known that the as-cast structure of the metal bar is such that cracking of the cast bar during hot forming may be a problem if the cast bar is required to be directly hot formed into a semi-finished product, such as redraw rod, during which the initially large cross-sectional area of the cast bar is substantially reduced by a plurality of deformations along different axes to provide a much smaller cross-sectional area in the product.
[0003] While this problem could be avoided by casting a cast bar having an initially small cross=sectional area which need not be substantially reduced to provide the desired cross-sectional area of the final product, this approach is not commercially practical for ferrous alloys since high casting outputs, and therefore low costs, can be readily achieved only with cast bars having large cross-sectional areas which are rapidly reduced to the smaller cross-sectional areas of the products, sumch as 3/8" diameter rod for drawing into wire, by a minimum number of severe deformations. Thus, the problem of a cast bar cracking during hot forming must be solved within the commercial context of cast bars having initially large cross-sectional areas which are then hot formed into products having small cross-sectional areas by a series of reductions which often are substantial enough to cause cracking of the cast bar under certain conditions.
[0004] This problem has been overcome in the prior art for relatively pure electrolytically-refined copper having low impurity levels such as 3-10 ppm lead, 1 ppm bismuth, and 1 ppm antimony. For example, U.S. Patent No. 3,317,994, and U.S. Patent No. 3,672,430 disclose that this cracking problem can be overcome by conditioning such relatively pure copper cast bar by initial large reductions of the cross-sectional area in the initial roll stands sufficient to substantially destroy the as-cast structure of the cast bar. The additional reductions along different axes of deformation, which would cause cracking of the cast bar but for the initial destruction of the as-cast structure of the cast bar, may then safely be performed. This conditioning of the cast bar not only prevents cracking of the cast bar during hot forming but also has the advantage of accomplishing a large reduction in the cross-sectional area of the cast bar while its hot-forming temperature is such as to minimize the power required for the reduction.
[0005] The above mentioned prior art has not, however, provided a solution to the cracking problem described above for metals, such as steel, containing a relatively high percentage of alloying elements. This is because the large amounts of alloying elements, often in the grain boundaries of the as-cast structure, cause the cast barto crack when an attempt is made to substantially destroy the as-cast structure with the same large initial reduction of the cross-sectional area of the cast bar that is known to be effective with relatively pure non-ferrous metal. Moreover, the greater the percentage of alloying elements in the cast bar, the more likely it is that cracks will occur during hot forming.
[0006] DE-A-2019700 describes a method of making thick metal sheet from continuously cast strand, in which the strand, immediately after casting, is subjected to compression whereby its cross section is reduced by seven to twenty percent, to allow the production of thick sheet of good quality.
[0007] GB-A-2014071 describes a method of continuously casting steel in which, for improving the internal quality and decreasing non-metallic inclusions in the cast product, the cast strand is ruled immediately after solidification at a reduction rate of 0.5 to 2.0 mm/m.
[0008] The object of the present invention is to provide a method of continuously casting molten steel and hot forming the cast steel, which eliminates substantial cracking of the cast bar during the hot ruling process.
[0009] The present invention resides in a method of continuously casting molten steel and hot forming said cast metal in substantially its as-cast condition at a hot-forming temperature by a plurality of substantial compressions, which method includes,
[0010] following casting of said metal and prior to said substantial compression of said metal, forming a substantially uniform fine grained or equiaxed structure at least at the surface of said metal by at least one preliminary light compression of said metal, characterised in that said light compressions comprise a first 7% reduction of the cross-section of said metal followed by at least one additional 7% reduction along an axis of compression 60° removed from the axis of said immediately prior 7% reduction.
[0012] The present invention makes it possible to hot form the cast bar at a hot-forming temperature into a product having a relatively small cross-sectional area by a substantial reduction of the cross-sectional area of the cast bar which would be such that the as-cast structure of the cast bar would be expected to cause the cast bar to crack, by first forming a substantially uniform subgrain structure at least in the surface layers of the cast bar prior to later substantial reduction of the cross-sectional area of the cast bar, said substantially uniform subgrain structure being formed by relatively light deformations of the cast bar while at a hot-forming temperature.
[0013] The light deformations are of a magnitude (preferably less than 30% in total) which will not cause the cast bar to crack, but which in combination with the hot-forming temperature of the cast bar will cause the cast bar to have a substantially uniform subgrain or cell structure of a thickness sufficient (about 10% of total area) to produce a bar of increased ductility when compared to a bar produced by the prior art process, which substantially inhibits the initiation of micro and macro cracking that normally begin at the as-cast grain boundaries, thus preventing cracking of the cast bar (even when having relatively high percentage alloying elements) during the subsequent substantial deformations. The substantially uniform subgrain structure of the surface provided by this invention allows substantial reduction of the cross-sectional area of the bar in a subsequent pass, even in excess of 30%, without cracking occurring and even though the cast bar has a relatively high amount of impurities or alloying elements.
[0014] For example, the present invention allows a steel alloy cast bar having a cross-sectional area of 32 cm2 (5 square inches), or more, and containing alloying elements, to be continuously hot formed into wrought rod having a cross-section area of 3 cm2 (1/2 square inch), or less, without cracking.
[0015] Furthermore, the invention has a wide general utility since it can also be used with certain other relatively impure or alloyed metals as an alternative to the solution to the problem of cracking described in U.S. Patent No. 3,317,994, and U.S. Patent No. 3,672,430.
[0016] The present invention can be used for continuously casting and hot-forming steel containing a relatively high percentage of alloying elements without using specially shaped reduction rolls in the hot-rolling mill or other complex rolling procedures.
[0017] The cast steel bar can be efficiently hot-formed using fewer roll stands following conditioning of the cast metal by first forming the described substantially uniform fine grained, equiaxed or cell structure at the surface of the cast metal, then hot rolling the modified structure by successive heavy deformations.
[0018] The present invention can be applied to a wide range of steel alloys, including by way of example:
low carbon 1015 (SAE) steel alloy, medium carbon 1045 (SAE) steel alloy, high carbon 1095 (SAE) steel alloy, free cutting carbon 1151 (SAE) steel alloy, corrosion and creep resistant A200 (ASTM) steel alloy, silicon spring 9259 (SAE) steel alloy, ball bearing 52100 steel alloy, martensitic stainless tool 440 C steel alloy, austenitic stainless 304 steel alloy, austenitic stainless 310 steel alloy, weldable stainless 348 steel alloy, ferritic freecutting 430F (SE) steel alloy, engine valve 14Cr-14Ni-2W steel alloy, precipitation hardening 17-7 PH steel alloy, tool steel 07 alloy, tool steel D5 alloy.
Preferably the substantial compression following the forming of said substantially uniform fine grained or equiaxed structure includes an initial compression providing at least 30% reduction of the cross-section of said metal.
In one preferred way of practising the invention, the plurality of preliminary light sequential compressions of said bar reduce the cross-section of said bar by a total reduction of less than 30%.
Further objects, features and advantages of the present invention will become apparent upon reading the following specification when taken in conjunction with the accompanying drawings.
Brief Description of the Drawing
[0019]
Fig. 1 is a schematic representation of casting and forming apparatus for practising the method of the present invention.
Fig. 2 is a representation cross-section of a cast bar in substantially an as-cast condition (in this case columnar).
Fig. 2A is a representation cross-section of a cast bar in substantially an as-cast condition (in this case equiaxed).
Fi. 3 is a representation cross-section of the cast bar shown in Fig. 2 following one light reduction of the cross-section.
Fig. 3A is a representation of a magnification of 2000x of the subgrain (cell or recrystallized) structure, a portion of which is shown in Fig. 3).
Fig. 4 is a representation cross-section of the cast bar shown in Fig. 2 following two perpendicular light compressions to form a complete shell of fine or equiaxed grains near the surface of the bar.
Fig. 5 is a representation cross-section of the cast bar shown in Fig. 2 following two light compressions and one severe hot-forming compression.
Best Mode for carrying out the Invention
[0020] Referring now to the drawing, in which like numerals refer to like parts throughout the several views, Fig. 1 schematically depicts an apparatus for practising the method of the present invention. The continuous casting and hot-forming system (10) includes a casting machine (12) which includes a casting wheel (14) having a peripheral groove therein, a flexible band (16) carried by a plurality of guide wheels (17) which bias the flexible band (16) against the casting wheel (14) for a portion of the circumference of the casting wheel (14) to cover the peripheral groove and form a mold between the band (16) and the casting wheel (14). As molten metal is poured into the mold through the pouring spout (19), the casting wheel (14) is rotated and the band (16) moves with the casting wheel (14) to form a moving mold. A cooling system (not shown) within the casting machine (12) causes the molten metal to solidify in the mold and to exit the casting wheel (14) as a solid cast bar (20).
[0021] From the casting machine (12), the cast bar (20) passes through a conditioning means (21), which includes roll stands (22) and (23). The conditioning roll stands (22) and (23) lightly compress the bar to form a shell of substantially uniform fine or equiaxed grain structure at the surface of the bar (20). After conditioning, the bar (20) is passed through a conventional rolling mill (24), which includes roll stands (25), (26), (27) and (28). The roll stands of the rolling mill (24) provide the primary hot forming of the cast bar by compressing the conditioned bar sequentially until the bar is reduced to a desired cross-sectional size and shape.
[0022] The grain structure of the cast bar (20) as it exits from the casting machine (12) is shown in Fig. 2. The molten metal solidifies in the casting machine in a fashion that can be columnar, or equiaxed, or both, depending on the super heat and cooling rate. This as-cast structure can be characterized by grains (30) extending radially from the surfaces of the bar (if columnar) and separated from each other by grain boundaries (31). Most of the alloying elements present in the cast bar are located along the grain and dendrite boundaries (31). If the molten steel alloy poured through the spout (19) into the casting wheel (14) were cooled and the cast bar (20) was passed immediately to the rolling mill (24) without passing through the conditioning means (21), the impurities along the boundaries (31) of the cast bar (20) would usually cause the cast bar to crack at the boundaries upon deformation by the roll stands of the rolling mill (24).
[0023] The conditioning means (21) prevents such cracking by providing a sequence of preliminary light compressions as shown in Fig. 3 and Fig. 4, wherein the result of a compression is shown and the previous shape of the cast bar is shown in broken lines. Fig. 3 shows the result of a 7% reduction provided by the roll stand (22) along a horizontal axis of compression (33). The columnar and/or equiaxed as-cast grain structure of the cast metal has been formed into a layer of substantially uniform fine grained, equiaxed or cell structure (35) covering a portion of the surface of the cast bar (20). The interior of the bar may still have an as-cast structure.
[0024] In Fig. 4 the bar (20) has been subjected to a second 7% reduction by the roll stand (23) along a vertical axis of compression (33) perpendicular to the axis of compression of roll stand (22). The volume of substantially uniform fine grained, equiaxed or cell structure (35) now forms a shell (36) around the entire surface of the bar (20), although the interior of the bar retains some as-cast structure.
[0025] It will be understood that the formation of the shell may be accomplished by a conditioning means comprising any number of roll stands, preferably at least two, or any other type of forming tools, such as extrusion dies, multiple forging hammers, etc., so long as the preliminary light deformation of the metal results in a substantially uniform fine grained, equiaxed or cell structure covering substantially the entire surface of the bar, or at least the areas subject to cracking.
[0026] The individual light deformations should be between 5-25% reduction so as not to crack the bar during conditioning. The total deformation provided by the conditioning means (21) must provide a shell (36) of sufficient depth (at least about 10%) to prevent cracking of the bar during subsequent deformation of the bar when passing through the roll stands (25-28) of the rolling mill (24).
[0027] When the shape of the bar in its as-cast condition includes prominent corners such as those of the bar shown in Fig. 2, the shape of the compressing surfaces in the roll stands (22) and (23) may be designed to avoid excessive compression of the corner areas as compared to the other surfaces of the cast bar, so that cracking will not result at the corners.
[0028] Fig. 5 shows a cross-section (20) following a substantial reduction of the cross-sectional area by the first roll stand (25) of the rolling mill (24). The remaining as-cast structure in the interior of the bar (20) has been transformed into a uniform fine grained, equiaxed or cell structure (35).
[0029] When a shell of improved structure (36) has been generated on the surface of the bar (20), a high reduction may be taken at the first roll stand (25) of the rolling mill (24). It has been found that such initial hot-forming compression may be in excess of 30% following conditioning according to the present invention. The ability to use very high reductions during subsequent hot-forming means that the desired final cross-sectional size and shape may be reached using a rolling mill having a few roll stands. Thus, even though a conditioning means according to the present invention requires one or more roll stands, the total amount and therefore cost of the conditioning and hot-forming apparatus may be reduced.
[0030] The method of the present invention allows continuous casting and rolling of relatively high percentage alloy steel, such as molybdenum and tungsten containing steels and austenitic steel alloys without cracking the bar. Furthermore, cracking is prevented throughout the hot-forming temperature range of the metal. Thus, the same casting and hot-forming apparatus may be used to produce steel alloys of varying purities and alloying elements depending on the standards which must be met for a particular product.
[0031] If it is desired to reduce even further the possibility of cracking, elliptically shaped rolling channels may be provided for all of the roll stands (22), (23), and (25-28) in order to provide optimal tangential velocities of the rolls in the roll stands with respect to the cast metal, as disclosed in U.S. Patent No. 3,317,994. However, such measures are usually not needed to avoid cracking if the present invention is practised as described herein on metals having alloy levels as described above.
1. A method of continuously casting molten steel and hot forming said cast metal in
substantially its as-cast condition at a hot-forming temperature by a plurality of
substantial compressions, which method includes,
following casting of said metal and prior to said substantial compression of said metal, forming a substantially uniform fine grained or equiaxed structure at least at the surface of said metal by at least one preliminary light compression of said metal, characterised in that said light compressions comprise a first 7% reduction of the cross-section of said metal followed by at least one additional 7% reduction along an axis of compression 60° removed from the axis of said immediately prior 7% reduction.
following casting of said metal and prior to said substantial compression of said metal, forming a substantially uniform fine grained or equiaxed structure at least at the surface of said metal by at least one preliminary light compression of said metal, characterised in that said light compressions comprise a first 7% reduction of the cross-section of said metal followed by at least one additional 7% reduction along an axis of compression 60° removed from the axis of said immediately prior 7% reduction.
2. The method of claim 1 wherein said metal is a low carbon 1015 (SAE) steel alloy.
3. The method of claim 1 wherein said metal is a medium carbon 1045 (SAE) steel alloy.
4. The method of claim 1 wherein said metal is a high carbon 1095 (SAE) steel alloy.
5. The method of claim 1 wherein said metal is a free cutting carbon 1151 (SAE) steel
alloy.
6. The method of claim 1 wherein said metal is a corrosion and creep resistant A 200
(ASTM) steel alloy.
7. The method of claim 1 wherein said metal is a silicon spring 9259 (SAE) steel alloy.
8. The method of claim 1 wherein said metal is a ball bearing 52100 steel alloy.
9. The method of claim 1 wherein said metal is a martensitic stainless tool 440 C
steel alloy.
10. The method of claim 1 wherein said metal is an austenitic stainless 304 steel
alloy.
11. The method of claim 1 wherein said metal is an austenitic stainless 310 steel
alloy.
12. The method of claim 1 wherein said metal is a weldable stainless 348 steel alloy.
13. The method of claim 1 wherein said metal is a ferritic freecutting 430F (SE) steel
alloy.
14. The method of claim 1 wherein said metal is an engine valve 14Cr-14Ni-2W steel
alloy.
15. The method of claim 1 wherein said metal is a precipitation hardening 17-7 PH
steel alloy.
16. The method of claim 1 wherein said metal is a tool steel 07 alloy.
17. The method of claim 1 wherein said metal is a tool steel D5 alloy.
18. The method of any preceding claim, wherein said substantial compression following
the forming of said substantially uniform fine grained or equiaxed structure includes
an initial compression providing at least 30% reduction of the cross-section of said
metal.
19. The method of any preceding claim, wherein the total of said light compressions
results in less than a 30% reduction of the cross-section of said metal.
20. The method as claimed in any preceding claim characterised in that the plurality
of preliminary light sequential compressions of said bar reduce the cross-section
of said bar by a total reduction of less than 30%:
the said bar is hot formed by a single compression of said bar to reduce its cross-sectional area by at least 40%; and
said bar is hot formed by a plurality of sequential compressions in each of which the cross-section of said bar is changed to the extent necessary to provide a hot-formed product having a predetermined cross-section.
21. The method of claim 20, wherein said conditioning of said bar includes passing
said bar between rolls in a plurality of sequential roll stands.
22. The method of claim 21, wherein said hot forming of said bar includes passing
said bar through sequential roll stands of a rolling mill.
1. Verfahren zum Stranggießen von flüssigem Stahl und zum Warmumformen dieses Gußmetalls,
im wsentlichen im gegossenen Zustand bei Warmumformtemperatur, durch mehrfaches starkes
Verdichten, wobei nach dem Gießen des Metalls und vor dem starken Verdichten desselben
ein im wesentlichen gleichmäßiges, feinkörniges oder gleichgerichtetes Gefüge zumindest
an der Oberfläche des genannten Metalls durch wenigstens eine leichte Vorverdichtung
des Metalls gebildet wird, dadurch gekennzeichnet, daß die leichten Verdichtungsvorgänge
eine erste siebenprozentige Querschnittsverminderung des Metalls gefolgt von wenigstens
einer weiteren siebenprozentigen Verminderung längs einer Verdichtungsachse umfassen,
die um 60° zur Achse der genannten, unmittelbar vorausgehenden siebenprozentigen Reduzierung
versetzt ist.
2. Verfahren nach Anspruch 1, wobei das Metall eine niedriggekohlte Stahllegierung
1015 (SAE) ist.
3. Verfahren nach Anspruch 1, wobei das Metall eine mitteigekohlte Stahllegierung
1045 (SAE) ist.
4. Verfahren nach Anspruch 1, wobei das Metall eine hochgekohlte Stahllegierung 1095
(SAE) ist.
5. Verfahren nach Anspruch 1, wobei das Metall eine Automaten-Kohlenstoffstahllegierung
1151 (SAE) ist.
6. Verfahren nach Anspruch 1, wobei das Metall eine korrosionsbeständige und kriechfeste
Stahllegierung A 200 (ASTM) ist.
7. Verfahren nach Anspruch 1, wobei das Metall eine Silizium-Federstahllegierung 9259
(SAE) ist.
8. Verfahren nach Anspruch 1, wobei das Metall eine Kugellager-Stahllegierung 52100
ist.
9. Verfahren nach Anspruch 1, wobei das Metall eine martensitische nichtrostende Werkzeugstahllegierung
440 C ist.
10. Verfahren nach Anspruch 1, wobei das Metall eine austenitische nichtrostende Stahllegierung
304 ist.
11. Verfahren nach Anspruch 1, wobei das Metall eine austenitische nichtrostende Stahllegierung
310 ist.
12. Verfahren nach Anspruch 1, wobei das Metall eine schweißbare, nichtrostende Stahllegierung
348 ist.
13. Verfahren nach Anspruch 1, wobei das Metall eine ferritische Automatenstahllegierung
430 F (SE) ist.
14. Verfahren nach Anspruch 1, wobei das Metall eine Motorventil-Stahllegierung 14Cr-14Ni-2W
ist.
15. Verfahren nach Anspruch 1, wobei das Metall eine aushärtbare Stahllegierung 17-7
PH ist.
16. Verfahren nach Anspruch 1, wobei das Metall eine Werkzeugstahllegierung 07 ist.
17. Verfahren nach Anspruch 1, wobei das Metall eine Werkzeugstahllegierung D5 ist.
18. Verfahren nach einem der Ansprüche 1 bis 17, wobei das genannte starke Verdichten
nach der umformung des im wesentlichen gleichmäßigen, feinkörnigen oder gleichgerichteten
Gefüges eine Vorverdichtung einschließt, die eine mindestens dreißigprozentige Querschnittsreduzierung
des Metalls bewirkt.
19. Verfahren nach einem der Ansprüche 1 bis 18, wobei die leichten Vedichtungen insgesamt
zu einer Querschnittsreduzierung des Metalls von weniger als 30 % führen.
20. Verfahren nach einem der Ansprüche 1 bis 19, dadurch gekennzeichnet, daß die Vielzahl
leichter, aufeinanderfolgender Vorverdichtungen des genannten Strangs den Querschnitt
des genannten Strangs insgesamt um weniger als 30% reduzieren, daß der Strang durch
einfache Verdichtung des Strangs derart umgeformt wird, daß sein Querschnittsbereich
um wenigstens 40% reduziert wird, und daß der Strang durch eine Vielzahl aufeinanderfolgender
Verdichtungsvorgänge umgeformt wird, bei denen der Querschnitt des genannten Strangs
jeweils soweit verändert wird, wie es erforderlich ist, um ein warmverformtes Erzeugnis
mit einem festgelegten Querschnitt zu erzielen.
21. Verfahren nach Anspruch 20, wobei die Bearbeitung des Strangs das Durchführen
des Strangs zwischen den Walzen einer Vielzahl aufeinanderfolgender Walzgerüste einschließt.
22. Verfahren nach Anspruch 21, wobei die Warmumformung des Strangs das Durchführen
des Strangs durch aufeinanderfolgende Walzgerüste eines Walzwerks einschließt.
1. Procédé de coulée en continu d'acier fondu et de formage à chaud de ce métal fondu
pratiquement en son état tel que fondu à une température de formage à chaud par une
série de compressions importantes, ce procédé comprend, après la coulée du métal et
avant la compression importante du métal, la formation d'une structure à grains fins
ou équiaxiale essentiellement uniforme au moins à la surface du métal par au moins
une légère compression préliminaire du métal, caractérisé en ce que les légères compressions
comprennent une première réduction de 7 % de la section transversale du métal suivie
d'au moins une réduction de 7 % additionnelle le long d'un axe de compression de 60
% éloigné de l'axe de la réduction de 7 % immédiatement précédente.
2. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier 1015 (SAE) à faible teneur en carbone.
3. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier 1045 (SAE) à moyenne teneur en carbone.
4. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier 1095 (SAE) à haute teneur en carbone.
5. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier 1151 (SAE) au carbone de décolletage.
6. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier A200 (ASTM) résistant à la corrosion et au fluage.
7. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier 9259 (SAE) de ressort au silicium.
8. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier 52100 pour roulement à billes.
9. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier 440 C pour outil inoxydable, martensitique.
10. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier 304 inoxydable austénitique.
11. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier 310 inoxydable austénitique.
12. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier 348 inoxydable soudable.
13. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier 430F (SE) de décolletage, ferritique.
14. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier de 14Cr-14Ni-2W pour soupape de moteur.
15. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
d'acier 17-7 PH de durcissement par précipitation.
16. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
07 d'acier pour outil.
17. Procédé suivant la revendication 1, caractérisé en ce que le métal est un alliage
D5 d'acier pour outil.
18. Procédé suivant l'une quelconque des revendications précédentes, caractérisé en
ce que la compression importante après la formation de la structure à grains fins
ou équiaxiale essentiellement uniforme comprend une compression initiale conférant
au moins 30 % de réduction à la section transversale du métal.
19. Procédé suivant l'une quelconque des revendications précédentes, caractérisé en
ce que le total des compressions légères précitées constitue une réduction de moins
de 30 % de la section transversale du métal.
20. Procédé suivant l'une quelconque des revendications précédentes, caractérisé en
ce que la série de légères compressions successives préliminaires de la barre réduisent
la section transversale de celle-ci d'une réduction totale de moins de 30 %, la barre
est formée à chaud par une seule compression de celle-ci pour réduire son aire transversale
d'au moins 40 % et la barre est formée à chaud par une série de compressions successives
au cours de chacune d'entres elles la section transversale de la barre est amenée
au taux nécessaire pour obtenir un produit formé à chaud ayant une section transversale
prédéterminée.
21. Procédé suivant la revendication 20, caractérisé en ce que le conditionnement
de la barre comprend le passage de celle-ci entre les cylindres d'une série de cages
de laminoir successives.
22. Procédé suivant la revendication 21, caractérisé en ce que le formage à chaud
de la barre comprend le passage de celle-ci par des cages de laminoir successives
d'un laminoir.