the following demands derive for the suitability of an alloy for an activation strip in an anti - theft security system , particularly for a system employing source tagging : the change of the remanence under bending or tensile stress should be optimally slight . a change of 20 % is prescribed as a guideline . as can be seen from fig3 values ≦ 10 % are achieved with the alloys of the present invention . it can be seen from fig4 that , in addition to being determined by the alloy , the coercive field strength and the bending radius also determine the change of the flux . given corresponding coercive field strengths , the alloys according to the present invention achieve values & lt ; 5 % given bending radii ≧ 12 mm or , respectively , values & lt ; 10 % given bending radii ≧ 4 mm and thicknesses of approximately 50 μm . the relationship of the saturation at a given , slight magnetizing field strength of , for example , 40 a / cm to the saturation bf given a magnetic field in the koe range should be nearly 1 , which can be seen from fig3 . the opposing field stability should be of such a nature that the remanence b s still retains at least 80 % of its original value after an opposing field magnetization of a few a / cm . finally , the remanence should retain only 20 % of the original value after a demagnetization cycle with a predetermined magnetic field . in detail , this means that a magnetization of the activation strip , i . e ., an activation / deactivation of the marker or display element , can also occur on site . however , only very small fields are generally available there . the saturation that is achieved should differ only slightly from the value given high magnetizing fields in order to guarantee identical behavior of the marker or display elements . the display elements or markers must be of such a nature that their remanence b r changes only slightly in the proximity of the coils in the detection locks as a consequence of a field that is elevated thereat and is potentially oriented in the opposite direction . as can be seen from fig1 the inventive alloys exhibit an opposing field stability as demanded . finally , the markers or display elements must be capable of being demagnetized with relatively small fields , i . e ., deactivated given magneto - elastic markers or , respectively , activated given harmonic display elements or markers . fig2 illustrates these relationships given the inventive alloys . simultaneously , meeting these last three demands yields extremely great limitations for the accessible ranges of the coercive forces h c , since the three demands are contradictory . the alloys of the present invention are typically manufactured by casting a melt of the alloy constituents in a crucible or furnace under a vacuum or a protective gas atmosphere . the temperatures thereby lie at approximately 1600 ° c . the casting typically utilizes a round ingot mold . the cast ingots of the present alloys are then typically processed by hot working , intermediate annealing , cold working and a further intermediate annealing . the intermediate annealing is performed for the purpose of homogenization , grain sophistication , shaping or the creation of desirable mechanical properties , particularly a high ductility . an excellent structure is achieved , for example , by the following process : thermal treatment at , preferably , temperatures above 800 ° c ., rapid cooling and annealing . preferred annealing temperatures lie at 400 ° c . through 600 ° c ., and the annealing times typically lie advantageously between one minute through 24 hours . a cold working corresponding to a cross - sectional reduction of at least 60 % before the annealing is , in particular , possible with the inventive alloys . the coercive force and the rectangularity of the magnetic b — h loop are enhanced by the step of annealing , and this is implemented for the demands made of the activation strips . the manufacturing method for especially good activation strips comprises the following steps : 2 ) hot rolling of the ingot at a temperature above 800 ° c . 3 ) multi - hour intermediate annealing at about 800 ° c . with quenching in water . 4 ) cold rolling corresponding to a cross - sectional reduction of approximately 90 %. 6 ) cold working corresponding to a cross - sectional reduction of approximately 90 %. 8 ) cold working to produce a cross - sectional rejection of approximately 70 %. activation strips that exhibited an excellent coercive force h c and a very good remanence b r were manufactured with this method . the magnetization properties and the opposing field stability were excellent . the manufacture of several embodiments of fe — ni — al — ti activation strips in accordance with the invention is described in detail on the basis of the following examples : an alloy with 18 . 0 weight % nickel , 3 . 8 weight % aluminum , 1 . 0 weight % titanium and the balance iron was melted under a vacuum . the resulting ingot was hot - rolled at approximately 1000 ° c ., intermediately annealed for one hour at 1100 ° c . and rapidly cooled in water . after a subsequent cold - rolling with a cross - sectional reduction of 80 %, the resulting ribbon was again intermediately annealed for one hour at 1100 ° c . and rapidly cooled in water . after a further cold working with a cross - sectional reduction of 50 %, the ribbon was intermediately annealed for four hours at 650 ° c . to provide a cross - sectional reduction of 90 %, the ribbon was subsequently cold - rolled and annealed at 520 ° c . for three hours and then cooled in air . a coercive force h c equal to 23 a / cm as well as a remanence b r equal to 1 . 48 t were measured . an alloy with 15 . 0 weight % nickel , 3 . 0 weight % aluminum , 1 . 2 weight % titanium and balance iron was processed as in example 1 but with the last intermediate annealing at 700 ° c ., the last cold working provided a cross - sectional reduction of 70 % as well as a final annealing was at 500 ° c . a coercive force h c equal to 21 a / cm and a remanence b r equal to 1 . 45 t were measured . an alloy with 15 . 0 weight % nickel , 3 . 0 weight % aluminum , 1 . 2 weight % titanium and balance iron was manufactured as in example 2 . deviating therefrom , the last intermediate annealing occurred at 650 ° c ., the last cold working to provide a cross - sectional reduction of 85 % and the annealing treatment was at 480 ° c . a coercive force h c equal to 20 a / cm and a remanence br equal to 1 . 53 t were measured . an alloy with 15 . 0 weight % nickel , 3 . 0 weight % aluminum , 1 . 2 weight % titanium , 2 . 0 weight % molybdenum and balance iron was manufactured as in example 2 . after an annealing treatment at 480 ° c ., a coercive force h c equal to 20 a / cm and a remanence b r equal to 1 . 56 t were measured . an alloy with 15 . 0 weight % nickel , 3 . 0 weight % aluminum , 0 . 8 weight % titanium and balance iron was melted under a vacuum . the resulting ingot was hot - rolled at approximately 1000 ° c ., intermediately annealed at 900 ° c . for one hour and rapidly cooled in water . after a following cold - rolling with a cross - sectional reduction of 90 %, the resulting ribbon was intermediately annealed for four hours at 650 ° c . to produce a cross - sectional reduction of 95 %, the tape was subsequently cold - rolled and annealed for three hours at 460 ° c . and then air - cooled . a coercive force h c equal to 14 a / cm and a remanence b r equal to 1 . 46 t were measured . an alloy with 15 . 0 weight % nickel , 2 . 5 weight % aluminum , 1 . 2 weight % titanium and balance iron was manufactured as in example 5 , but with a cross - sectional reduction of 83 % and an annealing treatment at 420 ° c . a coercive force h c equal to 17 a / cm and a remanence b r equal to 1 . 44 t were measured . an alloy with 20 . 0 weight % nickel , 1 . 0 weight % aluminum , 1 . 2 weight % titanium and the balance iron was melted under a vacuum . the resulting ingot was hot - rolled at approximately 1000 ° c ., intermediately annealed for one hour at 1100 ° c . and rapidly cooled in water . after a subsequent cold - rolling with a cross - sectional reduction of 80 %, the resulting ribbon was again intermediately annealed for one hour at 1100 ° c . and rapidly cooled in water . after a further cold working with a cross - sectional reduction of 50 %, the ribbon was intermediately annealed for four hours at 650 ° c . to provide a cross - sectional reduction of 75 %, the ribbon was subsequently cold - rolled and annealed at 450 ° c . for three hours and cooled in air . a coercive force h c equal to 13 . 4 a / cm as well as a remanence b r equal to 1 . 35 t were measured . an alloy with 15 . 0 weight % nickel , 1 . 3 weight % aluminum , 0 . 6 weight % titanium and the balance iron was melted under a vacuum . the resulting ingot was hot - rolled at approximately 1000 ° c ., intermediately annealed for one hour at 1100 ° c . and rapidly cooled in water . after a subsequent cold - rolling with a cross - sectional reduction of 80 %, the resulting ribbon was again intermediately annealed for one hour at 1100 ° c . and rapidly cooled in water . after a further cold working with a cross - sectional reduction of 50 %, the ribbon was intermediately annealed for four hours at 660 ° c . to provide a cross - sectional reduction of 85 %, the ribbon was subsequently cold - rolled and annealed at 550 ° c . for three hours and cooled in air . a coercive force h c equal to 17 . 3 a / cm as well as a remanence b r equal to 1 . 31 t were measured . a satisfactory magnetization behavior and a usable opposing field stability are derived in all exemplary embodiments . although various minor modifications may be suggested by those versed in the art , it should be understood that we wish to embody within the scope of the patent granted hereon all such modifications as reasonably and properly come within the scope of our contribution to the art .