Patent Application
20160145708
The invention relates to a method for producing a flat product from an iron-based shape memory alloy, in which a melt which comprises at least as a main component iron, alloying elements and unavoidable impurities is cast in a casting means to form a cast strip and in the process is cooled.
The prior art—for example, JP 62 112 751 A—reveals the possibility of producing foils or wires by strip casting methods. Strip casting sees the melt cast in a casting means wherein the casting region, or the holdup region in which the cast strip is shaped, is bounded on at least one longitudinal side by a wall which is advanced continuously during the casting operation and is cooled.
One example of a near-net-shape continuous casting method of this kind, and of a casting means for producing, for example, a flat steel product, is the two-roll casting means or “twin-roll caster”. In a twin-roll caster, in casting operation, two casting rolls or rollers oriented axially parallel to one another rotate in opposite directions and, in the region of their narrowest spacing, bound a casting gap which defines the casting region. These casting rolls are greatly cooled in the process, causing the melt which impinges on them to solidify to form in each case a shell. The rotational direction of the casting rolls is selected such that the melt and, together with it, the shells formed from it on the casting rolls are transported into the casting gap. The shells which enter the casting gap are compressed under the action of a sufficient strip-forming force to form the cast strip, with the consequence of an at least approximate complete solidification.
The principle used by the so-called belt casters is different. In a casting means of this kind, liquid steel is cast via a supply system onto a circulating casting belt, on which the steel solidifies. The running direction of the belt is selected such that the melt is conveyed away from the supply system. Disposed above the lower casting belt may be a further casting belt, which circulates in the opposite direction from the first casting belt. Irrespective of whether one or two casting belts are provided, in the case of the methods specified above as well, at least one casting belt borders the region in which the cast strip is formed. The respective casting belt is cooled intensively, and so the melt which comes into contact with the relevant casting belt solidifies thereon to form a strip, which can be taken off by the casting belt.
The cast strip emerging from the respective casting means is taken off and cooled, and can be passed on for further processing. This further processing may comprise a heat treatment and/or hot rolling. An advantage of strip casting is that the worksteps which follow strip casting can be run through in a continuous, uninterrupted sequence.
Known from the abovementioned Japanese laid-open specification JP 62 112 751 A is an iron-based shape memory alloy which apart from iron has elements in particular from the group “Mn, Si” and in which in addition to these elements there may be additional amounts of Cr, Ni, Co, Mo, C, Al, Ca and rare earth elements. From alloys with compositions of this kind, it is said to be possible, by strip casting, to produce cast foils which are temperature-stable and corrosion-resistant as well.
Against this background, it is an object of the present invention to propose cost-effective methods for producing flat products from an iron-based shape memory alloy that are bending resistant and are robust under pressure and torsion. The aim additionally is to produce a flat product which can be produced inexpensively and practically. Flat product is taken to encompass a cast and/or rolled strip or sheet and also plates, blanks, or the like that are obtained from such strip or sheet.
According to the first teaching of the method of the invention, the melt is cast to a strip in a casting means and cooled, ensuring the possibility of continuous casting operation, with the thickness of the strip being greater than 1 mm and less than 30 mm, and the casting region of said casting means being bounded at least on one of its longitudinal sides by a wall which moves in the casting direction during casting operation and which is cooled.
The strip thicknesses at which the cast and cooled strip of the invention leaves the casting gap, or is cast onto the casting belt, and solidifies are between more than 1 mm and 30 mm, more particularly between 1.5 mm and 20 mm, with further preference between 2 mm and 10 mm.
With the method of the invention it is possible to cast iron-based shape memory alloys as a flat product by means of a strip casting direction. In addition to the Fe—Mn—Si(—Cr(—Ni)) systems preferably employed, further systems are also conceivable, such as, for example, systems based on Fe—Ni, Fe—Ni—Al, Fe—Ni—Co—Ti, Fe—Ni—C, Fe—Ni—Nb, Fe—Ni—Si, Fe—Mn—Cr, Fe—Mn—Ni, Fe—Mn—Ni—Al, Fe—Mn—C, Fe—Mn—N, Fe—Cr—Si, Fe—Ga, Fe—Pd, Fe—Pt, Fe—Pd—Pt. On the basis of their use preferably for switching purposes, especially in high-temperature ranges, it is necessary to provide a material which meets the particular requirements. Depending on the utility, a material is used that has a minimum thickness of >1 mm, in order to be able to ensure the later component properties required, such as resistance to creasing and/or activity under bending resistance, for example.
According to a further refinement of the method, the casting means used is a twin-roll caster or a belt caster. It has emerged that the melt of the invention can be produced preferably via the stated strip casting means. Strip casting is outstandingly suitable for iron-based shape memory alloys, since relative to conventional casting, more particularly continuous casting, there is no need to use casting powder, and so it is possible to prevent casting problems occurring in the presence in particular of high levels of highly reactive alloying components, such as Mn, Si, Cr and/or Al, for example. Strip casting is further advantageous in particular if, for example, there are high alloying levels of highly segregating elements, such as Mn, Si, Cr and/or Ni, for example. Segregation can be substantially suppressed by rapid solidification. Furthermore, iron-based shape memory alloys have a low high-temperature ductility, and so the bending during casting is possible only for low thicknesses and/or is not absolutely necessary, depending on the casting means. A further characteristic is that iron-based shape memory alloys have a high hot forming resistance and are nevertheless thinly cast in substantially near-net-shape. The means can be used for the energy-efficient production of the flat product having shape memory properties. As already observed, in the case of a twin-roll caster, the axially parallel rolls each form a cooled boundary of the casting region, this boundary advancing continuously in the casting direction during casting operation, and this casting region being used to shape at least two longitudinal sides of the strip. Accordingly, a sufficiently high capacity can be provided with a single casting means, since the exit speeds of the cast strip are relatively high.
In the case of the belt caster, this function is taken on by a horizontally moving casting belt onto which the melt is cast to produce the strip. The advantage of using these belt casting means is that other method steps, such as hot rolling, for example, can follow on immediately and, in particular, the rolling effort is low, owing to the low casting thicknesses, and, on account of the compact nature of the casting means in question, an operating regime with the parameters required in terms of the material, especially with regard to the temperature, is possible in a particularly advantageous way. Since in a belt caster the melt is cast in the horizontal and cooled, the solidified strip undergoes no bending and, consequently, the stresses present in the strip itself are minor, thereby minimizing in particular the risk of cracks developing in the high-temperature region of the flat product produced.
It is advantageous, furthermore, if the melt, according to another refinement of the method of the invention, is cooled in contact with the moving wall or casting belt at a cooling rate of, in particular, at least 20 K/s, preferably 50 K/s, more preferably at least 100 K/s. The high speed of solidification allows a reduction to be achieved in segregation processes which have disadvantageous consequences for the material properties. The cooling rate is selected such that at the end of the casting operation, a solidified flat product is produced—for example, an iron-based strip composed of a shape memory alloy.
If an alloy-dependent roller pressure, expressed by what is called the RSF (roll separating force) or strip forming force (SFF), is set during casting with the twin-roll caster, it is possible to ensure substantially complete solidification right through the strip after emergence from the casting region, with high operational reliability. The specific roller pressure can be determined empirically and ensures a reliable strip casting operation.
If the strip passes through a warming apparatus prior to hot rolling, any heat loss occurring on emergence of the strip from the casting means can be compensated again, and the specific hot rolling temperature can be achieved in an operationally reliable way.
The strip speeds at which the cast strip emerges from the casting gap are in practice typically in the range from 0.06 to 3.0 m/s.
A particularly effective and economic production method can be provided by continuously supplying the cast strip emerging from the casting region to at least one rolling stand. The casting means may therefore directly supply at least one rolling stand with a cast strip for rolling, removing any need for handling of the cast strips between casting and rolling. Alternatively, the cast strip may also be cooled appropriately and heated again, if desired, at a later point in time, and rolled. Lastly, the hot strip is optionally cold-rolled, with the cold rolling taking place in at least one rolling pass.
In order to counteract embrittlement during the subsequent manufacturing and processing steps, it is possible in accordance with the invention to carry out an annealing treatment in hot-rolled and/or cold-rolled state at a temperature above the switching temperature for a period of 20 seconds to 48 hours.
An operationally reliable possibility for generating an iron-based flat product with shape memory effect provides for the strip emerging from the casting gap of the casting means, or the optionally cold-rolled strip which has solidified on the casting belt and subsequently, optionally, been additionally hot-rolled, to be heated, lastly, at least to the martensite finish (MF) temperature of the respective alloy. The flat product produced in this way allows the impression of a component design by corresponding loading of the flat product, in which case, during loading, the temperature is raised to at least austenite finish temperature (AF) and the load and the temperature >AF act on the flat product for at least 20 seconds. In the flat product of the invention, therefore, the shape memory effect is set to the desired component design.
After the casting of the strip, the cast strip can be subjected to hot rolling, in which case the initial hot-rolling temperature ought to be between 500° C. and TSolidus−50° C. As a result of the hot-rolling steps which follow the casting and cooling processes in line, it is possible on the one hand to set the desired final thickness of the strip and on the other hand to set the surface consistency, and also to optimize the microstructure, by, for example, closing cavities which are still present in the cast state. The hot strip can also be subjected to cold rolling and thereby reduced further in its thickness.
In order, in accordance with a further teaching, to provide a flat product composed of an iron-based shape memory alloy having reinforcements through intercrystalline atoms (group 1) or by mixed crystal solidification (group 2) or with a microstructure composed of austenite, ε-martensite, and fine precipitations in the form of carbides, borides, nitrides and/or a hybrid form thereof (group 1+group 2), the melt contains 10 to 45 wt % of manganese and up to 12 wt % of silicon, and at least one further element from a group 1, with group 1 encompassing the elements N, B, and C and with the following statement being valid for the alloying fractions of the group 1 in weight percent:
and/or comprises at least one further element from a group 2, the group 2 encompassing the elements Ti, Nb, W, V, and Zr and the following statement being valid for the alloying components of the group 2 in weight percent:
preferably ΣTi,Nb,W,V,Zr≧0.1%,
it being possible optionally for at least one, or two or more, of the following fractions of alloying components to be present:
P≦0.5 wt %, and/or
It has emerged that by near-net-shape casting methods, it is possible to produce flat products from an iron-based shape memory alloy that possess, depending on alloying components, reinforcements by intercrystalline atoms (group 1) or by mixed crystal solidification (group 2) or a microstructure of austenite, ε-martensite, and optionally fine precipitations (group 1+group 2). In this case, the alloys processed in each case in accordance with the invention have a composition such that the desired microstructure condition is reliably produced. It has emerged that flat products composed of iron-based shape memory alloys can also be cast to a cast strip via a casting means, allowing a near-net-shape flat steel product to be produced. In the case of the applied strip casting method, a strip is produced which comprises precipitation pairs in the form of carbides, nitrides, borides or a hybrid form thereof, on the basis, for example, of the amounts of the alloying constituents as per the group 1 N, C, B in conjunction with the elements of group 2, Ti, Nb, W, V, Zr, this strip providing the desired microstructure combination to achieve a shape memory effect, in conjunction with the iron, manganese, and silicon contents of the alloy. As a possible constituent, the alloy of the invention comprises at least one of the elements boron, nitrogen and/or carbon, and at least one of the elements titanium, niobium, tungsten, vanadium or zirconium, and, as the balance, iron, manganese, silicon and unavoidable impurities. The elements of groups 1 and 2 prove particularly advantageous since they lead to the desired precipitations, which serve as nucleus cells for the desired phase transformation at the corresponding sites. With the amounts of these elements as stated in the claims, the production method of the invention permits operationally reliable production of a flat product with shape memory effect. In the flat steel product produced in accordance with the invention, manganese in amounts of 12 wt % to 45 wt % promotes stabilization of the austenite in the material. In order to achieve this effect reliably, the Mn content may be situated between 20 wt % and in particular 35 wt %. Si contents of 1 wt % up to 12 wt % serve to ensure the reversibility of the transformation from martensite to austenite in the flat products of the invention. Preferred Si contents are 3 wt % to 10 wt %. Adjustments appropriate in practice for amounts of N, B, C and/or Ti, Nb, W, Zr come about when the C content is limited to a maximum of 0.5 wt %, more particularly to a maximum of 0.2 wt %. The B content is restricted appropriately to a maximum of 0.5 wt %, more particularly to a maximum of 0.05 wt %. The N content is restricted appropriately to 0.5 wt %, more particularly to a maximum of 0.2 wt %. Preferably, furthermore, the amount of elements of group 2 (Ti, Nb, W, V, Zr) is limited to a maximum of 2.0 wt %, more particularly to a maximum of 1.5 wt % individually. It may be advantageous for one or more of the elements of group 1 (N, B, C) to be added in each case in conjunction with one or more of the elements of group 2 (Ti, Nb, W, V, Zr) in the more narrowly confined amounts indicated, while the other elements of group 1 (N, B, C) are added within the maximum specification permitted in accordance with the invention. The same may also be true conversely for the two groups.
Although it is regarded as possible in accordance with the invention for the group of the alloying elements of an iron-based shape memory alloy of the invention to be confined, apart from Fe, Mn, Si and unavoidable impurities, to at least one element of group 1 and at least one further element of group 2, it may under certain circumstances be purposeful, for the setting of particular properties of the flat steel products obtained, to add, optionally, one or more of the elements from group Cu, Cr, Al, Mg, Mo, Co, Ni, O, P, S, Ca to the shape memory alloy. The contents ranges contemplated for this purpose in accordance with the invention in each case run as follows:
Cu: ≦20 wt %, preferably ≦10 wt %,
Cr: ≦20 wt %, preferably ≦10 wt %,
Al: ≦20 wt %, preferably ≦10 wt %,
Mg: ≦20 wt %, preferably ≦10 wt %,
Mo: ≦20 wt %, preferably ≦10 wt %,
Co: ≦20 wt %, preferably ≦10 wt %,
Ni: ≦20 wt %, preferably ≦10 wt %,
Through the addition of Cu, Mo and Co it is possible, individually or in combination, to improve the shape memory effect, whereas the effect of Cr, Al and Mg, individually or in combination, lies primarily in an improvement in the corrosion resistance. The individually stated elements may be alloyed in at up to 20 wt %, preferably up to 10 wt %. In order to avoid adverse effects of S, P and O, they are restricted to a maximum of 0.5 wt %, preferably a maximum of 0.2 wt %, more preferably a maximum of 0.1 wt %. Ni supports the stabilization of the austenite in the microstructure, and improves the formability of the material. When S is present, Ca may be alloyed in at not more than 0.5 wt %, in order to suppress unwanted binding of Mn in the form of MnS. The amount is restricted to a maximum of 0.5 wt %, preferably a maximum of 0.2 wt %, more preferably a maximum of 0.1 wt %.
In order to be able to utilize the positive effects of the optionally added alloying elements Cr and Ni, the melt may in each case optionally comprise at least 0.1 wt % of Ni and at least 0.2 wt % of Cr.
According to a further refinement, the shape memory alloy has the following alloying constituents in weight percent:
0.1 wt %≦Ni≦6.0 wt %, preferably 4.0 wt %,
Besides the stated possible components of the shape memory alloy, the alloying components Mn, Si, Cr, Ni and also one of the elements of group 1 (N, C, B) and/or one of the elements of group 2 (Ti, Nb, W, V, Zr), the shape memory alloy may further comprise the elements P, S, Mo, Cu, Al, Mg, O, Ca or Co, optionally, which at up to the stated values may develop advantageous effects. The precipitations which influence the shape memory effect and whose formation is influenced by the ratio of the two element groups, group 1 and group 2, to one another exhibit a significant, positive influence on the shape memory effect, provided the sum of the components of the elements of group 2 in atom % of the alloy, expressed as a ratio to the sum of the alloying components of group 1 in atom %, is in the range from 0.5 to 2.0. By this means a specific stochiometric ratio of the alloying elements of group 1 and group 2 is established. It has been found that with this ratio specifically for the alloying components in atom % of group 2 relative to group 1, the formation of precipitates is particularly favorable and supports the shape memory effect. If the stated ratio, for example, is less than 0.5, the precipitation elements may not be bound in the form of N, C and/or B and the shape memory effect is reduced, since the elements of group 1 are present in dissolved form in the microstructure. As a result, moreover, there is an adverse effect observed on the reversibility of the phase transformation, i.e., of the conversion from martensite back into austenite. If the ratio thus formed between the sums of the alloying constituents is greater than 2, unwanted solidifications come about, because of the elements of group 2, which are intercalated in the microstructure in the form of free atoms and thereby in turn hinder the shape memory effect.
The purpose of the manganese content of 25 wt % to 32 wt % is to stabilize the austenite in the microstructure, and it has an influence in particular over the switching temperature of the shape memory material. Below an Mn content of 25.0 wt % there is increased formation of ferrite, which is disadvantageous for the shape memory effect. If the Mn content is raised above 32 wt %, there is an excessive fall in the desired switching temperature, causing the switching temperature and the possible use temperatures of a corresponding component to be too close to one another.
Silicon serves to ensure the reversibility of the phase transformation from martensite into austenite. Contents below 3.0 wt % of Si lead to a reduction in the shape memory effect. Above 10 wt %, embrittlement of the material may be observed. At Si contents above 10 wt % moreover, there is increased formation of the unfavorable ferritic microstructure.
In order to ensure sufficient corrosion resistance, the shape memory alloy contains at least 3.0 wt % of Cr. An increase in the Cr content to above 10 wt % again promotes formation of ferrite, with its adverse consequences, as already stated, for the shape memory effect.
Nickel, lastly, serves to stabilize the austenitic microstructure and, moreover, improves the formability of the material. However, an Ni content of below 0.1 wt % has no significant effect on the properties of the material. Ni contents of more than 6.0 wt %, though, lead to slight improvements in the aforementioned properties, only in conjunction with an increased Cr fraction, and consequently, for cost savings, the Ni content is confined to a maximum of 6.0 wt %, preferably to a maximum of 4.0 wt %.
In order to ensure that the desired precipitations take place without adverse consequences for other properties of the shape memory alloy, a maximum of 0.1 wt % is envisaged as an upper limit for all of the elements of group 1, i.e., N, C, and B. The elements of group 2 (Ti, Nb, W, V, Zr) may be present at a minimum level of 0.01 wt %, this level applying at least to one element of this group. With a weight fraction of at least 0.01 wt %, preferably at least 0.1 wt %, for Ti, Nb, W, V and/or Zr, the shape memory effect is influenced positively. The reversibility of the phase transformation, in particular, can be ensured by a corresponding level of one of the group 2 elements. With preference each individual element of group 2 does not exceed the maximum level of 1.5 wt %, and more preferably the maximum amount of each individual element is 1.2 wt % or a maximum of 1.0 wt %, in order to counteract unwanted solidifications.
According to a first refinement of the shape memory alloy of the invention, the Cr content in weight percent is 3.0 wt %≦Cr≦10.0 wt %, thus achieving an effective compromise between ferrite formation and corrosion resistance of the shape memory alloy. Ferrite formation counteracts the shape memory effect, since ferrite does not enter into phase transformation and has a tendency toward premature plastic deformation.
According to a further refinement of the shape memory alloy, the difference between the Cr content and the Ni content is subject to the following relationship: 0 wt %≦Cr—Ni≦6.0 wt %. The maximum difference between the amounts of Cr and Ni is therefore limited to 6 wt %. It has emerged that an increase in the difference between the chromium and nickel contents to more than 6 wt % does not lead to any significant improvements in the mechanical properties, and instead leads to the embrittlement of the material. A drop in the difference to below 0 wt %, therefore meaning that the nickel content is greater than the chromium content, in contrast, may have adverse consequences for the switching temperature, by lowering it and causing it to come closer to the service temperature of the material.
According to one further refinement of the shape memory alloy, the ratio in atom % of the sum of the alloying components of group 1 and group 2 is subject to the following relationship:
and so on the one hand it is possible for the shape memory effect through sufficient formation of precipitations to be fully ensured and on the other hand it is possible for solidifications on the basis of free atoms of group 2 in the microstructure to be significantly reduced.
A further refinement of the shape memory alloy has N, C and/or B in the following amounts in weight percent:
If the shape memory alloy comprises the elements N and/or C in amounts of at least 0.005 wt % and/or B in an amount of at least 0.0005 wt %, these minimum amounts can be used to improve the formation of precipitations. Through the upper limit of 0.1 wt %, preferably of 0.05 wt %, more preferably 0.01 wt % of B, it is ensured that the oxidation resistance of the shape memory alloy does not drop too sharply. At the same time, the contents of N and C are each limited to a maximum of 0.1 wt %, preferably a maximum of 0.07 wt %, and so the precipitations do not become too great with the possible adverse consequences for mechanical properties of the alloy.
In a further refinement of the alloy, the alloy amounts of the alloying components of the elements of group 2 are limited. In accordance with this embodiment, the alloying components of the elements of group 2 are as follows:
Lastly, in accordance with a further embodiment of the shape memory alloy, sulfur, phosphorus, and oxygen ought to be limited to contents of not more than 0.1 wt %, preferably to not more than 0.05 wt %, and more preferably to not more than 0.03 wt %, in order to reduce their adverse influences, on corrosion resistance, for example. Molybdenum, copper, and cobalt can be alloyed in individually or in various combinations in order to improve the shape memory effect. A corresponding influence is limited in each case to contents of not more than 0.5 wt %. Aluminum and magnesium, individually or in combination, may contribute to an improvement in the corrosion resistance, and at the same time also bring about a reduction in the density of the alloy. Their amount is limited to a maximum of 5 wt %, preferably to a maximum of 2.0 wt %, more preferably to a maximum of 1.0 wt %.
According to a further refinement, calcium can be alloyed in for binding any sulfur present, in order to prevent unwanted binding of sulfur with manganese in the form of MnS. In order not to reduce the corrosion resistance and in order to prevent excessive impurities through Ca, the amount of Ca is limited to a maximum of 0.015 wt %, preferably to a maximum of 0.01 wt %.
According to a second teaching of the present invention, the object identified above is also achieved by a flat product with shape memory effect, consisting of an alloy which as well as iron and production-related impurities comprises manganese at 12 wt % to 24 wt %, silicon at 1 wt % to 12 wt %, and at least one further element of a group 1, the group 1 comprising the elements (N, B, C), and the alloying components of group 1 in weight percent being subject to the following relationship:
and/or there is at least one further element of a group 2, the group 2 comprising the elements (Ti, Nb, W, V, Zr), and the following relationship applying to the alloying components of group 2 in weight percent:
and the following fractions of alloying components may be present:
and the flat product has been strip-cast.
Further refinements, particularly of the alloy composition of the flat product of the invention, and manufacturing parameters for production, are evident from the above description of the production method.
The invention is to be elucidated in more detail hereinafter with reference to working examples in conjunction with the drawing.
The working examples listed in table 1 were cast using the casting means (twin-roll caster) shown in
The line 1 for producing a cast strip B comprises a casting means 2, which is constructed as a conventional twin-roll caster and, accordingly, has two rolls 3 and 4 which rotate oppositely to one another around axes X1 and X2 which are axially parallel to one another and are aligned at the same height. The rolls 3 and 4 are arranged with a spacing which sets the thickness D of the cast strip B to be produced, and so bound, at the longitudinal sides of the strip, a casting region 5, in the form of a casting gap, in which the cast strip B is shaped. At its narrow sides, the casting region 5 is sealed in a way which is also known, by means of side plates, not visible here, which are pressed against the end faces of the rolls 3 and 4.
During casting operation, the rolls 3 and 4, which are intensively cooled, for example, rotate and thus form a boundary at the longitudinal sides of a casting mold which is formed by the rolls 3 and 4 and by the side plates which move along continuously in casting operation. The direction of rotation of the rolls 3 and 4 is directed in this case, in the direction R of gravitational force, into the casting region 5, and so, as a consequence of the rotation, melt S is conveyed from a melt pool, in the space above the casting region 5, between the rolls 3 and 4, into the casting region 5. This melt S solidifies when it comes into contact with the circumferential surface of the rolls 3 and 4, on account of the intensive heat removal that takes place there, and forms a shell in each case. The shells adhering to the rolls 3 and 4 are conveyed by the rotation of the rolls 3 and 4 into the casting region 5, where they are pressed together under the effect of a strip-forming force SFF to form the cast strip B. The cooling output effective in the casting region 5 and the strip-forming force SFF are harmonized with one another in such a way that the cast strip B emerging continuously from the casting region 5 is very largely completely solidified.
The strip B emerging from the casting region 5 is first of all conveyed away vertically in the direction of gravitational force, and is subsequently bended in a known way, in a continuously curved arc, into a horizontally aligned conveying section 6. On the conveying section 6, the cast strip B may subsequently travel through a heating device 8, in which the strip B is heated to at least hot-rolling start temperature. The cast strip B heated accordingly is then rolled to form hot strip WB in at least one hot-rolling stand 9. Through targeted cooling 7 after the hot-rolling stand it is possible to influence the formation of the microstructure. By cooling of the strip to about 400° C., the coarsening of the precipitations can be suppressed. The hot strip WB can be subsequently coiled and otherwise prepared for onward transport.
Using the casting means shown in
The described heat treatment by means of the heating device 8, and the hot rolling with the hot-rolling stand 9, and the cooling step using the cooling device 7, are method steps that are merely optional.
The belt caster 1′ shown in
By way of the quenching 7 after hot rolling it is possible to set a desired microstructure in the strip, thus producing a flat product comprising a shape memory alloy, and this product can subsequently be coiled or otherwise prepared for onward transport.
It would be appreciated that a hot-rolling device, as depicted by way of example in
| Number | Date | Country | Kind |
|---|---|---|---|
| 13175870.8 | Jul 2013 | EP | regional |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/EP2013/065656 | 7/24/2013 | WO | 00 |
