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.:

 

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– 296 .

 

 

 

 

 

 

 

 

 

 

 

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.:

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., 2002. -348 .

 

RUS 2319956.

 

 

 

 

 

 

 

 

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/

. .,

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.15.03.2006.

 

 

 

 

 

 

 

 

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/

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-

 

 

 

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, . .

 

//

,

,

. –2007. –№ 7. –

. 55–55.

 

534:853.085332

1

2

 

1

2

-

 

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( )

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:

 

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1,

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2

 

.

.

 

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, akvor@yandex,ru

 

.

.-

.

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, vuaik@mail.ru

 

 

 

 

 

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[5,6].

 

 

 

 

 

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.1 ).

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)

 

 

 

)

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-19

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250

);

 

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, R = 2,29.10 3 / ); )

 

 

 

( )

 

 

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-

)

)

)

 

)

. 2.

V(Z)-

/ , ZN = 13,25

, ( V/V%)max = 68%,

 

Ge <111> ( R = 2,87 .103

 

1 .= 0,25 ,

– 1

.=11

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-22,

-

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213

1.

 

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// .,

., 1976, 336 .

2.

 

. .

-

 

//

.,

.

.., 1977, 120 .

 

 

 

 

 

 

3.

Weglein R.D., Wilson R.F. Acoustic microscopy of material and surface layers // J. Appl.

Phys., 1984. v.55. №9. p.3261-3275.

 

 

 

 

4.

Kustov A.I., Migel I.A. Investigation of

hysical-mechanical characteristics of glasses by

acoustic waves // Glass Physics and Chemistry, 1996 - v.22 - № 3, . 245-247.

 

 

 

5.

.

.,

. .

ё

 

 

-

 

 

//

, №2 (155), 2010, .9 – 14.

 

 

 

 

 

 

 

6.

.

.,

. .

 

,

 

 

 

 

,

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-

 

., .13., №4., 2016.,

. 490 - 496.

 

 

 

 

7.

 

. .,

. .,

. .

 

 

 

 

 

.

.:

., 1981., 197 .

 

 

 

534:853.085.332

1

2

3

1,2

. .

 

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3

.-

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,

 

, akvor@yandex,ru

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, akvor@yandex,ru

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, vuaik@mail.ru

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( ., % = 19,64394,

= 311,184 . 106

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[5].

 

 

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:

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: 20

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;

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. 38

);

)

 

 

 

 

 

 

 

 

 

 

 

 

 

(40

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ё

 

 

 

 

 

 

 

 

 

 

 

 

 

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.

 

 

 

 

 

 

 

 

 

 

 

-

 

 

 

 

 

 

 

 

 

 

 

 

 

 

1. Weaver J.M.R., Ilett C., Somekh M.G., Briggs G.A.D. Acoustic microscopy of Solid Mate-

rials // Metallography . 1985 . V.17 . . 3-34.

 

 

 

 

 

 

 

2.

 

.

.,

 

. .

//

 

 

 

.

.

-

 

 

 

 

 

 

-

 

 

 

 

3.

 

.

.,

. -

. .

, 2013.– . 18.-

.4.

 

2. – 612

. ( .1875-1877).

 

 

 

 

 

 

 

 

 

 

-

 

–

 

 

//

.

.

.

.,

11, №4/2., 2014. – . 592 -598.

 

 

-

 

 

4.

 

. .

 

. .

 

 

 

 

 

 

 

 

,

 

 

 

 

 

 

//

 

 

 

 

-

.

.

.

.

 

. –

, 2016. – .21. –

.3. – 1464

. ( . 1097-1101).

 

 

 

5.

 

 

 

 

:

/ . .

 

,

. .

,

.;

/

. .

 

 

. .

 

. –

.;

, 1991. – 1232 .

 

 

 

6. AddaY.,et. al. La diffusion dans les solids. Paris:Press Univers. de France, 1966, vol.2., p.

87-95.

215

669.14.017:620.181

 

1

 

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3

 

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.

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1, . .

 

2, . .

3

 

 

 

 

.- .

,

 

, akvor@yandex,ru

 

 

.

.

,

 

, akvor@yandex,ru

 

 

 

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.-

.

,

, vuaik@mail.ru

,

 

 

 

 

 

 

 

 

 

 

 

 

 

 

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[2].

 

-

 

 

 

 

,

 

 

 

 

 

 

 

 

.1 .

 

 

 

 

 

 

 

 

 

 

 

 

 

 

 

.

( V/V%

R)

 

 

 

 

 

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,

 

 

 

 

 

 

 

.1

)

 

 

 

 

 

 

-

 

 

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,

 

 

 

V(Z)-

 

 

 

 

 

 

R

 

 

),

 

–

 

 

.

R,

,

-

V(Z)-

 

 

 

 

-

 

 

 

 

E

G,

 

,

-

.

V(Z)-

[2].

216

 

)

 

)

 

 

 

)

 

 

.1.

 

 

 

 

 

 

 

 

 

50%,

 

 

 

 

 

 

(

 

 

 

; 2 , Z = -14

,

40

/

.) – );

(

)

V(Z)-

30

( R = 3,18 .103 /

, ZN = 14,68

, ( V/V%)max = 37%,

,

 

(

780

0 ), 120

 

,

 

1

.=0,25

 

 

 

– 1

.=12,2

 

)

 

 

 

 

)

 

 

 

)

 

. 2.

 

R

(

),

30

( R = 3,18.103

/ , ZN

= 14,68

;

( V/V%)max

(

0)

 

 

( )

-

 

(

 

 

1)

 

 

 

 

 

 

 

 

 

(

.3

).

 

 

 

 

 

 

)

 

 

 

 

)

 

 

 

.3.

 

7,7 %/

.)

 

Cu-

 

 

 

 

 

 

 

 

 

380 °

– 50 °

 

 

 

(Cu –

; =1,1

, l =70

;

)

 

 

 

 

 

 

-

 

 

 

 

 

 

 

 

 

.

 

 

 

1.

, . .

 

 

 

 

/ .

 

, .

//

.

. . /

. .

. –

.:

, 1976. –

. 17–66.

 

 

 

2.

.

.,

. .

 

 

 

 

 

 

-

-

–

 

//

,

11, №4/2., 2014. –

. 592 -598.

 

 

-

 

217

539.67 : 539.32 : 538.951

NI-FE-GA

. .

 

 

1, . .

 

 

2,

. .

3, . .

4

 

1

 

.

.- .

, . .

., k.sapozhnikov@mail.ioffe.ru

 

 

 

 

-

 

 

 

. .

 

.

,

-

,

 

 

 

 

 

,

 

-

 

,

 

 

 

2

.

.- .

, .

.

.,

. ., nkvlad@inbox.ru

 

 

 

 

 

 

 

3

.

.- .

, .

.

., V.Krymov@mail.ioffe.ru

 

 

 

 

 

 

-

 

 

 

. .

 

.

,

-

,

 

4

 

.

.- .

,

 

 

, Sergey.Kustov@uib.es

 

 

 

 

 

 

 

 

 

,

 

 

 

 

,

,

 

 

 

 

,

 

 

 

 

Ni55Fe18Ga27,

 

 

 

 

 

 

 

 

 

100

 

 

 

12

- 370

 

 

 

 

 

10-7 -

10-4.

 

 

 

 

 

 

 

 

 

,

 

 

 

 

 

 

 

 

 

,

.

 

 

 

 

.

 

 

 

 

 

 

 

 

 

 

 

 

 

 

 

 

 

 

:

Ni-Fe-Ga,

 

 

,

 

,

,

,.

Ni-Fe-Ga alloys belong to a family of functional ferromagnetic shape memory alloys. Thermal treatment along with composition changes are the simplest means of controlling the

functional properties of Ni-Fe-Ga alloys. Changes in the degree of atomic order and precipita- tion of phase are usually considered as factors determining the properties of Ni-Fe-Ga al-

loys, while the role of point defects, in particular, quenched-in vacancies, is either ignored or analyzed in terms of their impact on the ordering process. However, point defects are among the main factors affecting the mobility of linear and planar defects and thereby the functional properties of alloys. Recently, we have found that quenching of Ni55Fe18Ga27 single crystals from an annealing temperature to the martensitic phase leads to a phenomenon of hyperstabilization of the martensitic phase that has been explained by sweeping of quenched-in point defects by moving interphase boundaries during reverse transformation [1]. It has been also shown that the concentration of vacancies in a Ni-Fe-Ga alloy changes upon thermal treatment in very broad limits and reaches up to 2500 ppm in samples quenched from high tem-

peratures [2].

This work is devoted to study of the elastic (effective Young´s modulus) and anelastic

(linear and non-linear internal friction, Young's modulus defect, anelastic strain) properties of Ni55Fe18Ga27 alloy, subjected to different heat treatments, by means of resonant piezoelectric composite oscillator technique at frequencies around 100 kHz, temperatures of 12-370 K and strain amplitudes between 10-7 and 10-4. Samples were cut from rod-shaped Ni55Fe18Ga27 single crystals with [100]A orientation along the rod. After annealing for 20 min. at 970 K, the samples were subjected to three different heat treatments: 1) slow cooling in the air; 2) direct quenching into room-temperature water; 3) step-quenching (quenching into oil at 390 K followed by quenching into room-temperature water). The samples cooled in air were characterized by the forward and reverse martensitic transformation temperatures about 330 and 340 K, respectively, and the Curie temperature of Tc = 290 K. The samples directly quenched into water were in a hyperstabilized state, where a small fraction of martensite exhibited reverse transformation near 400 K, while the main fraction required overheating up to a temperature about 580 K [1]. The magnetic transformation after quenching becomes smeared and shifts to

218

Tc ≈ 270 K. The martensitic phase of the alloy, as analyzed by TEM, presents at room temperature a mixture of 7-layered (14M) and non-modulated (2M) structures.

It has been shown that elastic and anelastic properties of the Ni-Fe-Ga alloy depend crucially on the thermal treatment because of strong pinning of twin boundaries by quenchedin point defects. The amplitude dependence of the internal friction, Young's modulus defect and amplitude of reversible anelastic strain demonstrates stages corresponding to motion of twin boundaries inside extended point defect atmospheres, breaking the twin boundaries through the atmospheres and their oscillations outside the atmospheres [3]. It is concluded that vacancies form atmospheres near twin boundaries, the density of which (but not their extension) strongly depend on the concentration of vacancies. Two stages are revealed in the temperature dependences of the elastic and anelastic properties of the alloy that can be associated with pinning/depinning of twin boundaries by/from different point defects, most probably divacancies and monovacancies. Experimental data evidence that point defect diffusion is defect-assisted, proceeding largely within lattice regions adjacent to twin boundaries over the entire temperature range under study. Studying the effect of temperature on the amplitude dependence of anelastic properties of the alloy enables us to follow the evolution of the point defect distribution in atmospheres around twin boundaries.

This work was supported by Ministry of Education and Science of the Russian Federation, project no. 3.1421.2017/4.6.

1.Kustov S. Mechanical spectroscopy of hyperstabilized martensites / S.B. Kustov, R.

Santamarta, E. Cesari, K. Sapozhnikov, V. Nikolaev, V. Fedorov, V. Krymov, J. Van Humbeeck // Solid State Phenom. – 2012. - V. 184. - P. 355–360.

2.Unzueta I. Experimental observation of vacancy-assisted martensitic transformation shift in Ni-Fe-Ga alloys / I. Unzueta, D. Alonso de R-Lorente, E. Cesari, V. Sánchez-Alarcos, V. Recarte, J.I.

Pérez-Landazábal, J.A. García, F. Plazaola // Phys. Rev. Lett. - 2019. - V. 122. - P. 165701 (1-7).

3.

. .

 

 

 

//

Ni55Fe18Ga27 / . .

, . .

, . .

, . .

- 2019. - . 45. - . 6. -

. 43-46.

 

 

219

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