PRODUCTION SYSTEM OF WELDABLE AND STAINLESS TUBULAR STRUCTURES WITH HIGH MECHANICAL STRENGTH AND PRODUCT OBTAINED THEREFROM
A production system weldable and stainless tubular structures with high mechanical strength and related obtained product, particularly for making tubular elements in cold-drawn stainless steel, workable at different thicknesses and shapes, provided with high performances in terms of mechanical characteristics and weldability, for the construction of light and ultralight structural frames destined for a dynamic use. It comprises a creation step of a tip for making the end of the tube smaller, so that it can pass through the drawing equipment and be coupled for drawing, a step of annealing heat treatment for softening the material and making it deformable. The system provides a mechanical test for evaluating the mechanical characteristics of the material and a metallography for viewing the structure of the material and evaluating if it comes within pre-established parameters for the drawing and a chemical preparation of the surfaces, for lubricating the contact surfaces of the tube with the drawing equipment and for avoiding seizures during the drawing. The preceding steps are repeated until the desired thickness. A step of final heat treatment follows, for reforming the structure of the steel and for fixing the desired final characteristics. Finally, a step of straightening is carried out for make the drawn and furnace-treated tube rectilinear, and a step of passivation for inducing a compact oxide patina ensuring its resistance to corrosion. The cutting, control and packaging operations follow.
The present invention refers to a production system of weldable and stainless tubular structures with high mechanical strength and product obtained therefrom, particularly indicated for making cold-drawn stainless steel tubular elements, workable with different thicknesses and shapes, provided with high performances in terms of mechanical and weldability characteristics for the construction of light and ultralight structural frames destined for a dynamic use, such as for example those for competition vehicles like race cars, high-end bicycles and for aeronautics.
In particular, the structural frames mentioned above are those for which particular performances are requested, in addition to strength and reliability, of lightness and good behaviour in the presence of dynamic stresses, as is the case of the structures for competition vehicles and for aeronautics.
As is known, the steel structural frames for dynamic use traditionally consisted of multi-way tubes, made with different steel qualities, welded together or interconnected by metal connection elements.
One dynamic frame example is that employed for making bicycles.
The making of tubes, destined for high-end bicycle frames, requires that they are subjected to particular working (shaping and differentiation of the thicknesses, also along the same tube, by means of broaching and/or coning) so to obtain a weight reduction, while ensuring a good mechanical strength even near the weld, and to increase the consistency of the structure, conferring greater stiffness and not only for aesthetic and design reasons.
As already mentioned, the tubes in question are preferably connected to each other by means of welding. To make good level connections, maintaining the mechanical characteristics of the material even in the weld zone, it is necessary to weld with particular techniques. A first welding example used is that called TIG (where TIG stands for Tungsten Inert Gas). In TIG welding, an electric arc is used for heating and melting the metal: the electric arc is started between the electrode and the piece to be welded. A protection gas passes through the nozzle, protecting the welding bath and the tungsten electrode. The main object of the protection gas in TIG welding consists of protecting the hot zones and the melted zones of the piece, the weld material and the electrode from the negative influence of the surrounding air. Moreover, the protection gas influences the characteristics of the arc and the aesthetics of the weld. The TIG welding advantages include the high quality of the joints and the absence of slag and spatter. Another welding method is braze-welding. These techniques require a high degree of precision and involve refined welding methods even if considered of artisan type.
Other, more technologically evolved welding methods are known, such as electron beam or laser welding which are used for the production of components for the aeronautics and aerospace sectors but which are not employed in the bicycle sector.
In fact, for example, the electron beam welding can join two materials even of different nature with high precision, which causes perfect adhesion between them without requiring a weld line. But in addition to requiring a very high initial investment cost, and the use of electricity, the costs exponentially increase in proportion with the size of the object to be welded, resulting hence unacceptably high.
In addition to that illustrated above, the electron beam welding and laser welding are not adapted for joining pieces of a certain size, such as frames, and are so costly and demanding that they require excessive investments to be used in the sector of bicycle frame producers. Moreover, after the welding, the finished frame requires an additional heat treatment with consequent movement costs etc. which considerably increase the production costs.
In every case, the used welding techniques must not induce yielding or other situations of vulnerability, nor aesthetically negative effects.
Presently, all qualities of steel adapted for the construction of the frames mentioned above lead to problems of weakening of the mechanical characteristics at the welding site, which oblige the application of reinforcement elements near the junctions, or the use of tubular elements of greater thicknesses (excluding the steel tubular elements welded with the electron beam and laser techniques).
Other problems in the construction of dynamic frames emerge from the fact that, today, the most employed steel typologies (i.e. carbon steels like 25CrMo4), while having optimal mechanical properties, are subject to corrosion, which causes both external and internal deterioration of the tube with obvious negative consequences regarding the strength and durability. In order to prevent deterioration, protection and finishing interventions are necessary which consist of protective paints, which in any case do not protect the tube interior where the corrosion is destined to occur if not through special, costly technologies.
Due to the use of protective enamels, negative effects are produced with regard to the weight, in addition to overall environmental impact induced from the production and maintenance of the frame.
Among special non-stainless steels, capable of giving high performances in terms of elasticity, strength and lightness requirements, there is for example the steel 15CrMoV6, which is nickel-plated rather than painted; the corrosion protection is ensured in this case both outside and inside the tube. With the nickel-plating treatment, it is necessary to take into account the multiple negative effects which if not well controlled could cause further drawbacks. In fact, in the nickel-plating treatment, the negative impact is known which the electroplating activity has on the environment, due to the emission of various toxic substances, like heavy metals, cyanides and strong acids (sulphuric acid, hydrochloric acid) with high environmental impact. The use of mineral salts, caustic substances and solvents in rather high quantities are a problem regarding both the waste waters and the waste disposal. Moreover, the formation of toxic vapours and powders coming from the working produces a considerable impact on the air.
Among other material not subject to corrosion, excluding aluminium and titanium (which do not belong to the category of materials referred to here and which have a series of specific, unresolved problems) and the ferritic stainless steels (characterised by poor mechanical characteristics and being liable to oxidation), a response to such problems was sought in the last decade in the stainless steels which however have not to date attained characteristics which are overall adequate for needs.
In fact, the austenitic stainless steels (such as for example AISI 304, AISI 308 etc.) have optimal weldability and stainless characteristics but poor mechanical properties; they are ductile but not hard, and (being monophasic) do not take to hardening: in fact, even with a fast cooling, after heating to temperatures greater than the transformation point (AC3), they do not change structure, remaining austenitic.
To confer greater mechanical characteristics to them, the stainless steels can be hardened with the treatment by mechanical stress (such as drawing, for example).
In this case, however, the problem tied to the welding step remains unresolved. By heating the material above the melting point, the neighbouring zones are also heated (and thus softened), which thus lose the acquired mechanical characteristics. The weld zone is configured as a further weak point. The attainable thinning of the thickness, to ensure strength to the structure, does not permit lightening the weight in an appreciable amount. Moreover, once hardened by drawing (or another mechanical stress), this type of steel has complex additional working problems.
While the chrome-nickel stainless steels cannot be hardened, the chrome martensitic stainless steels can be hardened.
In other words, in this type of steel, the austenite solubilised during the heat treatment and subjected to quick cooling generates a martensitic structure, attaining high mechanical characteristics.
The martensitic steel with Cr percentages greater than 13%, moreover, optimally resists corrosion. However, also in this case, problems arise tied to the welding step since in welding all martensitic steels are subject to the formation of microcracks (and in fact it is advisable to avoid this operation on steels with greater than 0.20% carbon content) which even if imperceptible compromise the strength, above all in the case of structures to be subjected to dynamic stresses. In any case, since they are self-hardening steels, it is always necessary to carry out a preheating before the welding and a tempering or an annealing immediately afterward. This aspect makes this material unfit and costly for the creation of tubes to be welded for the construction of greatly stressed frames for competition vehicles or for aircraft.
Presently on the market, there are also stainless steels hardening by precipitation (steel 17-4PH) which have good stainless steel qualities and have alloy elements (such as Al, Nb, Ti, Mo, Cu) such to cause, after the heat-aging treatment, the precipitation of hardening phases within the matrix, with the goal of bringing said steels to a high mechanical strength accompanied by a moderate tenacity and ductility.
As with the martensitic steels, these types of steels are also not easily subsequently reworkable, if not at very high costs.
Moreover, also in this case, the problem of weldability remains unresolved, since in the welding step the precipitation of the carbides is not produced. The formation of weak points during welding consequently makes the final structure less reliable.
Such problem can be avoided only with a further heat treatment, subsequent to the welding step, but which would lead to working problems with consequent additional costs.
Alternatively to the described steels, other stainless materials have been examined for the sector (such as, for example, the AerMet 100 alloy). The mentioned materials are characterised by more than one alloy element being present in greater than 5%, though they are not considered “alloys”, intended in the traditional sense, but “super alloys” based on iron, cobalt, nickel (i.e. alloys in which the different mechanisms of structural modifications, which regulate the attainment of particular properties, are not due exclusively to the content of the additional elements but also to the complexity of the alloy itself).
In particular, these materials have a low modulus of elasticity and are of considerably more complex working than that required by steel. With such material, tubes are made, also drawn but always obtained by means of plate welding (and therefore never by billet extrusion). In addition to complex working and heat treatments, once made in a specific diameter and thickness (like the materials already described), they can no longer be modified if not at costs which would make the production uneconomical. Moreover, the consolidation of the frame points close to the weld must be carried out with the application of external reinforcement elements (gaskets).
A final mention is made, for the sake of completeness, to the possible production of tubes in Nanoflex, innovative steel obtained by nanotechnology, which thus has a completely different structure from the other steel categories.
It is a material which has considerable potentialities for the high mechanical characteristics (which are not obtained by heat treatments but by reduction percentage): theoretically, the tubes made in this steel can attain the best mechanical, workability and finish characteristics examined up to now. But, apart from the fact that even Nanoflex has several problems during welding, this material is not yet commercially available.
Object of the present invention is substantially that of resolving the problems of the prior art by overcoming the above-described difficulties by means of a production system of weldable and stainless tubular structures with high mechanical strength and product obtained therefrom, capable of making tubes which cannot be attacked by corrosion, provided with high mechanical strength, easily workable for the obtainment of different thicknesses and shapes and easily weldable with limited weakness inductions near the weld.
A second object of the present invention is that of making a production system of weldable and stainless tubular structures with high mechanical strength and product obtained therefrom, capable of offering an improved technological response for the construction of light structural frames and welded tubular structures destined for dynamic use, obtained with tubes without welding and therefore structurally homogenous.
A third object of the present invention is that of having a production system of weldable and stainless tubular structures with high mechanical strength and product obtained therefrom which is capable of making tubes with high mechanical properties and optimal safety and quality standards, destined to give an improved technological response for making mechanical components subject to dynamic stresses, for use also in extreme conditions in which high performance characteristics are required, in sectors such as aerospace, aeronautics, nuclear, chemical, marine, motor sports and cycling.
Another object of the present invention is that of making a production system of weldable and stainless tubular structures with high mechanical strength and product obtained therefrom which has a high index of workability.
A further object of the present invention is that of making a production system of weldable and stainless tubular structures with high mechanical strength and product obtained therefrom which permits reducing many of the environmental problems tied to the entire lifecycle of the object: reducing the processes in the production step and consequent consumption of toxic-harmful substances; in the useful lifetime steps of the object ensuring the lengthening of the durability, raising of the safety conditions and eliminating the use of chemical substances for maintenance; and at the end of the useful lifetime, in the discard step, ensuring the total recyclability without any loss of the raw material characteristics (as instead occurs in the recycling of the soft metals).
Not the least object of the present invention is that of making a production system of weldable and stainless tubular structures with high mechanical strength and product obtained therefrom which is simply made and has a good functionality.
These objects and still others, which will appear more clearly in the course of the present description, are substantially attained by a production system of weldable and stainless tubular structures with high mechanical strength and product obtained therefrom, as claimed below.
Further characteristics and advantages will be more evident from the detailed description of a production system of weldable and stainless tubular structures with high mechanical strength and product obtained therefrom, according to the present invention, made here below with reference to the attached pictures, provided only as indicative and hence non-limiting, in which:
The process of the present invention provides for the use of a steel which can be defined, for its characteristics, as “austenitic-martensitic”; in fact, its specific chemical composition has a carbon content and molybdenum content of an austenitic stainless steel, and a nickel and chromium content of a martensitic stainless steel. The austenitic-martensitic steel according to the invention will have a martensitic percentage which can even arrive at about 95%. For this reason, the process of the invention can also be applied to martensitic steel. One type of steel which can be advantageously employed in the process of the invention is that called X4CrNiMo 16-5-1.
The production system of weldable and stainless tubular structures with high mechanical strength of the present invention is substantially composed of the following steps:
-
- hot working of a martensitic steel or austenitic-martensitic steel to make a rough tube (known as a “preform”);
- creation of a tip which serves to make the end of the tube smaller, so that it can pass through the drawing equipment and can be coupled for drawing,
- annealing heat treatment which serves to soften the material and make it deformable,
- optionally, a mechanical test which permits establishing if the mechanical characteristics of the material are suitable for subjecting the tube to drawing,
- optionally, metallography which permits viewing the structure of the material to evaluate if it comes within already established parameters, so to be able to proceed with the drawing, otherwise the material must undergo an annealing operation for softening it so it can be worked,
- chemical preparation of the surfaces which serves for lubricating the contact surfaces of the tube with the drawing equipment and for preventing seizures,
- drawing which deforms the material in a permanent manner,
- final heat treatment which serves for reforming the structure of the steel which was deformed and for determining the desired final characteristics,
- straightening which serves for making the drawn and furnace-treated tube rectilinear,
- passivation which serves for inducing a compact oxide patina into the steel, which ensures its resistance to corrosion.
The process can then be completed by conventional passages such as the cutting of the tube thus produced into more easily manageable pieces, quality control and packaging.
The first step of the process is the obtainment of the “preform”, which is the raw material from which one starts for carrying out the process according to the present invention. In more detail, the preform is a tube which is hot-worked (at about 1300° C.): it can be rolled with the wheels which form it or extruded with a press. The characteristics of the preform are typical of a working carried out at high temperature: oxidised surfaces, coarse tolerances, large thicknesses with respect to the diameter, possibility of having only standard dimensions.
The preform is composed of material at the hardened and tempered state, whose high mechanical strength would not permit its drawing. In order to reduce its mechanical strength, it is necessary to subject it to an annealing process in one step if in a static furnace (or shaft furnace, load furnace etc.) or in several steps if in continuous or muffle furnaces, with the goal of passing it through the drawing machine and thus reduce its diameter and thickness.
The annealing heat treatment used in the production system of the present invention is carried out in controlled atmosphere furnaces for avoiding that the material undergoes surface alterations, both externally and internally, and prevents any oxidation and decarbonation. With the term “controlled atmosphere” it is intended an atmosphere of inert gases (such as nitrogen, helium, argon, etc.) or a vacuum atmosphere. In particular, a particularly advantageous controlled atmosphere in the scope of the present invention is a gaseous mixture composed of about 50% nitrogen and about 50% reducing gas, in which the reducing gas is for example a gas containing hydrogen such as that obtainable by steam reforming.
More in detail, in the annealing heat treatment step which is carried out in continuous type furnaces, one must account for the weight of the tube, the speed and time of passage and the temperature in the different zones of the furnace in order to obtain the desired technical characteristics in the working material. The heat treatment is a preparation treatment of the material for the subsequent steps and workings.
The annealing step provides for a first heating step from ambient temperature to the annealing temperature, a treatment step at the annealing temperature and a cooling step.
The preheating from ambient temperature to the annealing temperature is carried out in times of generally less than 1 hour.
The annealing treatment is carried out at a temperature which varies between 600° C. and 750° C., preferably between 650° C. and 700° C. In particularly preferred embodiment of the invention, the annealing treatment is carried out at a temperature of about 680° C. The annealing treatment will be extended for a time of at least 40 minutes, preferably at least 1 hour, more preferably less than 3 hours. In a particularly preferred embodiment of the invention, the annealing treatment will be extended for about 1 hour and 20 minutes. The combination of treatment temperature and time is essential in order to obtain a material having the desired characteristics, i.e. high weldability together with optimal mechanical properties. In general, it can be affirmed that the treatment temperature is inversely proportional to the treatment time: if one operates at a temperature close to the lower limit of the above-outlined range, it will therefore be necessary to prolong the treatment times.
The cooling of the annealed tube is an extremely important operation. A slow cooling in a controlled atmosphere is essential. Generally, cooling times are provided for between 2 and 4 hours.
Optionally, in order to verify that the material has the required characteristics and specifications for the subsequent steps, it is subjected to a mechanical test which permits establishing if the mechanical characteristics of the material are suitable for subjecting the tube to drawing and metallography for evaluating if the structure of the material comes within already established parameters, so to be able to proceed with the drawing; otherwise, the material will have to undergo an annealing treatment to soften it so it can be worked. These controls will not be routinely carried out, however, but only in the implementation step of the process on the selected martensitic or austenitic-martensitic steel. The normal operations of the invention process do not require these steps.
At this point, the material is ready for the subsequent step which consists of the step of chemical preparation of the surfaces. The step in question consists of the immersion of the tube in a first tub containing a suitable acid (of nitric-hydrofluoric type) for a predetermined time (on the order of 40 minutes), rinsing in water in a second tub and a subsequent immersion in a bath of an oxalate salt for a pre-established time (on the order of 20 minutes) and a final immersion in a stearic ester (preferably in 3% by weight concentration) which serves for lubricating the outer surface of the tube. Preferably, for the acid treatment, 140 kg/m3 are used of 56% nitric acid and 40 kg/m3 of 38-40% hydrofluoric acid. For the oxalate treatment, the oxalate concentration will generally be in the range of 8-16% by weight.
At this point, the material is ready for the step of drawing, since the tip for engaging the tube to the equipment of the drawing machine was made at the beginning of the work cycle.
Drawing is a mechanical working which permanently deforms the materials, in the present case steel. It is executed cold and therefore at ambient temperature by means of a machine (the drawing machine) which forces the material, drawing it by one end, to pass through the drawing equipment which determines its final configuration. The drawing equipment, in the case of tubes, can be made to work both on the tube exterior and interior. The steel drawn by one end takes the form of the equipment in which it is drawn and made to pass through.
In the present production system, all of the equipment must be made of “hard metal” with greater strength characteristics than those of the material being worked.
In particular, in the drawing step of the invention, several passages are executed in order to obtain the desired thicknesses of the tubes, since at each passage one succeeds to obtain a thickness reduction of about 20%. The drawing speed also depends on the material thickness: in fact, if one starts with 5 mm-1.75 mm thicknesses, the drawing speed is moderate while with smaller thicknesses it is lower.
The above-described drawing is that with mandrel, but other drawing technologies are obviously not excluded, like bar drawing or cold pilger rolling.
After every passage through the drawing machine, the material is preferably subjected to a subsequent heat treatment with a passage in a furnace, since otherwise the material would break with the risk of inclusions. Such heat treatment, called normalisation, is particularly advised once thin thicknesses of the tube have been reached (thicknesses less than 2 mm for a tube diameter of about 5 cm).
The material, before entering the furnace, is subjected to a cleaning operation for removing the lubricating residues. The cleaning is carried out by immersion in tubs containing a solution of surface-active substances and carbonate salts.
The normalisation is normally conduced at a temperature in the range of 950° C.-1150° C. for a time greater than 10 minutes and less than 1 hour.
The material is generally subjected to different steps of drawing, cleaning, normalisation by furnace heat treatment and chemical preparation of the surfaces until the desired thickness is obtained.
Once the desired thickness of the tube is reached, the material is subjected to the step of final heat treatment which gives the mechanical characteristics to the material (mechanical strength, yield and elongation).
The final heat treatment of normalisation and stress relieving occurs—always in controlled atmosphere—with temperatures and stay times set as a function both of the geometry of the finished tube and the final mechanical and desired microstructural characteristics. The normalisation, as said above, will be carried out at temperatures in the range of 950° C.-1150° C. for a time greater than 10 minutes and less than 1 hour. It should be taken into consideration that for tube thicknesses greater than 2 mm longer treatment times could be necessary than for lesser thicknesses.
In the last normalisation step, the cooling modes are very important in order to determine a high quality product. Such heat treatment process is very different from the traditional heat treatments with cooling in oil carried out in traditional chamber or muffle furnaces. In fact, for cooling the steel more quickly, at present the incandescent steel (900° C.) is immersed in ambient temperature oil. The oil's capacity to exchange heat is very high (the oil does not evaporate at 900° C.) and there is therefore a drastic cooling. In this case, however, the surface of the tubes is in contact with oil and there is a “contamination” which causes oxidation, so that the tubes would require a tempering heat treatment which cannot be achieved on tubes with small thicknesses (less than 1 mm) since they would irreparably deform.
In accordance with the present production system, after the heat treatment, a step of rapid cooling is preferably carried out which operates by means of forced cooling on the controlled atmosphere around the tube (in detail, the tube is not in contact with the cooling water) and a step of gradual cooling until the tube is brought to ambient temperature.
In particular, a refrigerated controlled atmosphere is used, for example by placing, inside the cooling zone downstream of the furnace, a cold-water jacket or tubing near the working tubes.
With an air cooling according to the prior art, the heat is more slowly eliminated from the steel and the cooling is slower, but with the above-described modifications carried out on the facility, a sufficient cooling speed is attained. In this case one is able to work in a controlled atmosphere, thus avoiding ruining the surfaces of the tubes. It is important that the tube being worked undergoes a sudden temperature lowering, from about 920° C. (temperature at the furnace outlet) to about 450° C., in a time in the range of 30 seconds-2 minutes, preferably about 1 minute.
In addition to the foregoing, the heating of the material serves so to be able to bring the steel to have a specific starting structure, chosen as a function of the desired end product.
Moreover, the stay time serves to ensure a certain homogeneity: i.e. since the entire volume of the steel is homogeneous and has the same structure.
Finally, the cooling serves to obtain specific structures and hence mechanical characteristics: as a function of the cooling speed, one can obtain different structures.
The production system according to the present invention, at this point, provides for the step of straightening the tube, to which the step of pickling and/or passivation follows. In this step, the tube is treated so to induce a compact chromium oxide patina onto the steel, which ensures its resistance to corrosion. The methods used are conventional and consist of an acid treatment with acid baths like those described above (pickling), followed by washing and by subsequent immersion in a less aggressive acid bath (for example, diluted nitric acid) to induce a passivation speed.
At this point, the tube is subjected to the step of cutting, in which it is brought to the desired length as a function of the subsequent structural needs and is then packaged for storage and sale. The cutting can also be advantageously carried out before the pickling and passivation step.
In the production system of the present invention, the previous operations are all carried out with a controlled atmosphere to prevent the oxygen from coming into contact with the tube surfaces, since at high temperatures the oxidation process is very reactive and amplified.
Once the production of the tube with the invention system has been completed, when two or more elements must be joined in order to obtain a frame, shown in
The present invention thus attains the aimed objects.
In fact, the production system of tubular structures of the invention permits obtaining a tubular element with high mechanical properties and high quality and safety standards, destined to give the best technological response for making mechanical components subjected to dynamic stress, for uses even in extreme conditions, in which considerable performance characteristics are required in sectors such as aerospace, aeronautics, nuclear, marine, chemical, motor sports and cycling.
Moreover, the production system of tubular structures of the invention permits obtaining:
-
- an improvement of the quality of the structure, since in the final drawn tube the crystallographic structure is preserved of a martensitic steel but which is further improved, as shown in
FIG. 1 where one sees a fine and homogenous structure (due to the heat treatment of normalisation in a controlled atmosphere), thus ensuring structural characteristics, and in particular strength to the final product which are appreciably better than both those of the starting material and those obtainable with the traditional heat treatments, in oil or water, which require a tempering heat treatment which can be difficult or even impossible to make on tubes of small thicknesses, as already mentioned above; - a surface finish, outside and inside the tube, which is greatly improved with respect to the conventionally-treated tubes, as shown in
FIG. 11 where there is a comparison between the two stainless tubes of the same type, one of which treated with oil and the other with the system of the invention with air: the first results deformed and slightly opaque, the second has maintained the original form and is perfectly glossy; - maintenance of the size and shape characteristics;
- a reduction of the working waste and discards, the inevitable drawbacks with the traditional and current heat treatments are avoided, such as: discard formation due to deformations and breaking, need for further final treatment of tempering/stress relieving, need for final inner/outer surface treatment for removing the inevitable stains from heat and oxidation, shown in
FIG. 11 , and which require mechanical satin finishing or chemical work by means of acid attacks; - a reduction of the negative environmental impact: in fact, the overall environmental impact of the production process is reduced since there are no more problems related to the disposal of the oil of the traditional heat treatments and of the acid substances necessary for the satin finishing operations, rendered obsolete by the quality of the obtained final product, which in order to be stabilised with high stainless characteristics, requires only a light process of passivation at the end of the cycle.
- an improvement of the quality of the structure, since in the final drawn tube the crystallographic structure is preserved of a martensitic steel but which is further improved, as shown in
In addition to that illustrated up to now, with the production system of the invention the negative impact is reduced tied to the need of paints. Moreover, with respect to common steels, the recovery and recycling of the material is considerably increased.
Advantageously, the system according to the present invention permits maintaining high weldability characteristics (as shown in
The absence of microcracks explains how, during the mechanical traction tests, the overly stressed structure did not break at the weld but along the non-welded line of the tube (i.e. in the base material), as shown in
Normally, the break points are determined at the welds (or near these), since greater material vulnerability is created due to the formation of microcracks, which create weak points.
To overcome this problem, and to confer greater safety conditions near the weld itself, one normally employs the solution of making differentiated thicknesses along the tube, increasing its thickness in these points or by applying reinforcements.
On the other hand, the weld quality obtained in the tubes described here simplifies the working process and also introduces new opportunities, permitting using the process of shaping with differentiated thicknesses according to new criteria, process destined to give different levels of desired stiffness (specific stiffness) in different points of the elements assembled together in order to improve the geometric stability of the frame while further reducing the weight.
To support the improved mechanical characteristics of the product obtained with the production system according to the present invention, a comparison was carried out between two of the best typologies of steels currently on the market and the product obtained with the system of the invention. The following table shows the obtained results.
General characteristics:
The high modulus of elasticity of 211,000 Mpa—twice the value of that of a titanium tube and three times that of aluminium—permits making extremely light frames with a high degree of stiffness.
The optimal expansion coefficient—in the field 20÷100° C.≦0.00001 mm—ensures optimal geometric and dimensional stability of the structure during the useful lifetime.
Advantageously, the steel obtained with the present system is stainless and weldable with extremely reduced thicknesses, since the steel of the weld and that in the surrounding areas has the mechanical characteristics of the rest of the structure as it is heated during welding and then quickly cooled.
In addition to that shown above, the steel obtained with the production system according to the present invention can be worked with already existing machines and tools and with known technologies, permitting considerable savings in the tubular structure production costs.
Advantageously, with the system of the present invention, numerous environmental impact problems tied to the entire life cycle of the object are not encountered. In fact, in the production step the system involves a reduction of the processes and consequent consumption of toxic-harmful substances with respect to that which occurs in the prior art; in the useful lifetime steps of the object, a greater durability and an increase of the safety conditions are ensured, and the use of chemical substances for maintenance is eliminated; at the end of the useful life, in the discard step, total recyclability is ensured without any loss of the raw material characteristics (as instead occurs in the recycling of soft steels).
In addition to that stated up to now, the production system is quite versatile and is capable of offering a production with decidedly innovative and reliable characteristics, given that the tubular element is obtained by a billet-extruded material, it is hence without welding and is cold-drawn. Moreover, the tubular element puts together the high technical performances of the martensitic steels with the high weldability characteristics of the austenitic steels, and is therefore optimally weldable with TIG and MIG technologies of known type and without elaborate processes as occurs in the prior art to obtain welds with high strength and seal characteristics.
In particular, as already anticipated above, the obtained tubular element has high strength characteristics (1.000÷1.300 MPa), high modulus of elasticity (211,000 MPa, twice that of a titanium tube and three times that of an aluminium tube), an optimal dimensional stability (20÷100° C.−0.0001 mm) and therefore geometric stability ensured over the time of use, it is easily workable for the obtainment of the most varied shapes and thicknesses and has an excellent surface finish, in addition to the fact that, being highly stainless, it is free from degradation and wear over time.
Not the least advantage of the present invention is that the steel tube according to the invention is considerably practical in use, easy to make and with good functionality.
Naturally, numerous modifications and variations can be made to the present invention, all coming within the scope of the characterising inventive concept.
Claims
1. Production system of weldable and stainless tubular structures with high mechanical strength, comprising the following steps in succession:
- annealing heat treatment of a preform in martensitic or austenitic-martensitic steel,
- chemical preparation of the surfaces for lubricating the contact surfaces of the tube with the drawing equipment,
- at least one drawing passage for deforming the material in a permanent manner.
2. Production system of tubular structures according to claim 1, comprising a step of final heat treatment for reforming the structure of the steel which was deformed and for determining the desired final characteristics.
3. Production system of tubular structures according to claim 1, comprising at least two drawing passages until the pre-established thickness is reached.
4. Production system of tubular structures according to claim 1, wherein in every drawing passage the thickness is reduced by about 20%.
5. Production system of tubular structures according to claim 1, comprising, before said at least one drawing passage, a step of normalisation heat treatment of said tubular structure.
6. Production system of tubular structures according to claim 5, wherein said step of normalisation heat treatment is conducted at a temperature in the range of 950° C.-1150° C. and for a time greater than 10 minutes and preferably less than 1 hour.
7. Production system of tubular structures according to claim 1, wherein said annealing step of the preform in martensitic or austenitic-martensitic steel provides for a first step of heating from ambient temperature to the annealing temperature, a step of treatment at the annealing temperature and a step of cooling, and wherein said step of treatment at the annealing temperature is conducted at a temperatures selected in the range of from 600° C.-750° C., preferably 650° C.-700° C.
8. Production system of tubular structures according to claim 7, wherein said annealing treatment is carried out at a temperature of about 680° C.
9. Production system of tubular structures according to 7, wherein said annealing treatment is extended for a time of at least 40 minutes, preferably at least 1 hour and preferably less than 3 hours.
10. Production system of tubular structures according to claim 9, wherein said annealing treatment is extended for about 1 hour and 20 minutes.
11. Production system of tubular structures according to claim 8, wherein said step of heating from ambient temperature to the annealing temperature is conducted in a time less than or equal to 1 hour.
12. Production system of tubular structures according to claim 8, wherein said step of cooling is conducted in a time in the range of 2-4 hours.
13. Production system of tubular structures according to claim 1, wherein said step of chemical preparation of the surfaces comprises the immersion of the tubular structure in a first tub containing an acid for a pre-established time, preferably on the order of 40 minutes, rinsing in water in a second tub and subsequent immersion in a bath of a oxalate salt for a predetermined time, preferably on the order of 20 minutes, and final immersion in a stearic ester, preferably in a concentration of 3% by weight for lubricating the external surface of the tubular structure.
14. Production system of tubular structures according to claim 13, wherein, for the acid treatment, 140 kg/m3 of 56% nitric acid and 40 kg/m3 of 38-40% hydrofluoric acid are used and wherein, for the treatment with oxalate, the oxalate concentration will be generally in the range of 8-16% by weight.
15. Production system of tubular structures according to claim 2, wherein said step of final heat treatment is conducted at a temperature in the range of 950° C.-1150° C. and for a time greater than 10 minutes and less than 1 hour.
16. Production system of tubular structures according to claim 15, wherein said final heat treatment is followed by a step of rapid cooling and then by a step of slow cooling.
17. Production system of tubular structures according to claim 16, wherein said step of rapid cooling is conducted by means of the contact of said tubular structure with a refrigerated, controlled gaseous atmosphere.
18. Production system of tubular structures according to claim 16, wherein said step of rapid cooling provides for the temperature lowering of said tubular structure from about 920° C. (temperature at the furnace outlet) to about 450° C., in a time in the range of 30 seconds-2 minutes, preferably about 1 minute.
19. Production system of tubular structures according to claim 2, wherein said tubular structure, before said final heat treatment step, is subjected to a cleaning operation for removing the lubricating residues.
20. Production system of tubular structures according to claim 19, wherein said cleaning step is carried out by immersion in a solution of surface-active substances and carbonate salts.
21. Production system of tubular structures according to claim 1, wherein said heat treatments of annealing, normalisation and final heat treatment are executed in controlled atmosphere furnaces to avoid that the material undergoes surface alterations, both externally and internally, and to prevent any oxidation and decarbonation.
22. Production system of tubular structures according to claim 21, wherein said controlled atmosphere is a gaseous mixture consisting of about 50% nitrogen and about 50% reducing gas, wherein the reducing gas is preferably a gas containing hydrogen such as that obtainable by steam reforming.
23. Production system of tubular structures according to claim 1, wherein said preform is a rough tube obtained by hot-working from a billet or other source of martensitic or austenitic-martensitic steel, preferably by extrusion.
24. Production system of tubular structures according to claim 1, wherein said tubular structures, after said step of final heat treatment, are subjected to a step of pickling and/or passivation.
25. Tubular structure in martensitic or austenitic-martensitic steel, weldable and with high mechanical strength, obtainable by means of the process according to claim 1.
26. Tubular structure according to claim 25, wherein said steel is X4Cr—Ni—Mo 16-5-1.
27. Tubular structure according to claim 25, wherein said steel has a tensile strength >1100 N/mm2.
Type: Application
Filed: Mar 23, 2007
Publication Date: Nov 12, 2009
Inventor: Serena Omodeo Sale' (Milano)
Application Number: 12/293,594
International Classification: C21D 9/08 (20060101); C22C 38/22 (20060101);
