Information recording method and system using a magneto-optical medium

Abstract: A magneto-optical recording medium includes a substrate on which light is incident, a first magnetic layer provided at the substrate side, and a second magnetic layer provided on the first magnetic layer. The first magnetic layer is an in-plane magnetization film at a room temperature and transits to a perpendicular magnetization film at a temperature between room temperature and a Curie temperature thereof. The second magnetic layer has a Curie temperature lower than that of the first magnetic layer and is a perpendicular magnetization film. A direction of magnetization of the first magnetic layer is anti-parallel to a direction of magnetization of the second magnetic layer in a state in which the first magnetic layer and second magnetic layer are stable each other by exchange-coupling.

Description: The present invention relates to a magneto-optical recording method and system. As a rewritable high-density recording method, a magneto-optical recording medium on which information is recorded by writing magnetic domains on a magnetic thin film using heat energy of a semiconductor laser, and from which the information is read out using the magneto-optical effect has received a lot of attention. In recent years, demand has arisen for realizing a larger-capacity recording medium by increasing the recording speed of the magneto-optical recording medium. The line recording density of an optical disk such as a magneto-optical recording medium largely depends on the laser wavelength of a reproduction optical system and the numerical aperture of an objective lens. More specifically, when the wavelength λ of the reproduction optical system and the numerical aperture NA of the objective lens are determined, the diameter of the beam waist is determined. For this reason, the lower limit of a mark period which can be reproduced and detected is about λ/2NA. On the other hand, the track density is mainly limited by crosstalk. The crosstalk is mainly determined by the distribution (profile) of a laser beam on the medium surface, and is expressed by a function of λ/2NA as in the mark period. Therefore, in order to realize a high density in a conventional optical disk, the wavelength of a laser of the reproduction optical system must be shortened, and the numerical aperture NA of the objective lens must be increased. However, it is not easy to shorten the wavelength of the laser due to problems associated with efficiency, heating, and the like of elements. On the other hand, when the numerical aperture of the objective lens is increased, the distance between the lens and the disk becomes too small, and a mechanical problem such as a collision occurs. For these reasons, a technique for increasing the recording density by magnetic super-resolution by modifying the arrangement or the reading method of a recording medium has been developed. For example, in Japanese Laid-Open Patent Application No. 3-93058, after the direction of magnetization of a reproducing layer is aligned in one direction using an initialization magnetic field before reproduction of a signal, a signal held in a recording layer is transferred to the reproducing layer while applying a reproducing magnetic field so as to reduce intersymbol interference upon reproduction, and to allow reproduction of a signal having a period smaller than the diffraction limit of light, thereby improving the line recording density and the track density. Also, in recent years, demand has arisen for increasing the recording speed. The conventional recording method for a magneto-optical recording method requires three processes (erasure of old data, recording of new data, and verification of whether or not new data is normally recorded) upon recording. For this reason, the disk must complete three revolutions to rewrite information, and requires a long time to rewrite information accordingly. For this reason, overwrite methods (an optical modulation method and a magnetic field modulation method) for directly recording new data on old data by omitting the erasure process from the three processes have been proposed and extensively studied. Of these methods, the magnetic field modulation method cannot increase the recording capacity by adhering two disks to each other since a magnetic field must be applied from a side opposite to the light incidence side, and the magnetic modulation speed of a magnetic head is limited. For these reasons, it is difficult to increase the recording speed. On the other hand, the optical modulation method performs recording by forming magnetic domains by modulating a laser beam. In this method, two media can be adhered to each other to achieve a large capacity, and the switching speed of a laser is higher than the magnetic field modulation speed of the magnetic head, thus easily increasing the recording speed. Therefore, when information recording is performed by the optical modulation overwrite method, and information is reproduced by the above-mentioned super-resolution, a large amount of information can be recorded. However, in the above-mentioned magneto-optical reproduction method based on the super-resolution, the direction of magnetization of the reproducing layer must be aligned in one direction before irradiation of a laser beam. For this reason, a magnet for initializing the reproducing layer must be added to the conventional apparatus. Therefore, this reproduction method suffers the following problems. That is, the magneto-optical recording apparatus is complicated, has high cost, is difficult to achieve a compact structure, and so on. In order to simultaneously achieve the super-resolution medium and the optical modulation overwrite technique, three or more magnetic layers in principle, and six or more magnetic layers in practice are required. Therefore, the layer structure is complicated, and it is difficult to reduce cost and to improve quality. The present invention has been made to at least alleviate the above-mentioned problems, and has as its object to provide a magneto-optical recording method and system which require neither an initialization magnetic field nor a reproduction magnetic field upon reproduction, which use a medium having a simple layer structure constituted by two or more layers in principle, which allow reproduction of a signal having a period equal to or smaller than the diffraction limit of light with a high S/N (C/N) ratio, and allow recording by the optical modulation overwrite method. In order to achieve the above object, there is provided a method of recording onto a magneto-optical recording medium as defined in claim 1 and a system of recording as defined in claim 4. A medium as defined in the preamble of claim 1 is known from EP-A-0509836. A number of embodiments of the invention will now be described, by way of example only, with reference to the accompanying drawings in which: Fig. 1 is a sectional view showing an example of the basic structure of magnetic layers in a magneto-optical recording medium of an embodiment of the present invention; Fig. 2 is a sectional view showing another example of the basic structure of magnetic layers in the magneto-optical recording medium of an embodiment of the present invention; Figs. 3A to 3C are views showing an example of a reproduction method of the magneto-optical recording medium of an embodiment of the present invention, in which Fig. 3A is a view showing a mask region and an aperture region in a light spot on the medium surface, Fig. 3B is a view showing the state of the directions of magnetization of the respective layers, and Fig. 3C is a graph showing the temperature distribution in the track direction; Figs. 4A to 4C are views showing another example of the reproduction method of the magneto-optical recording medium of an embodiment of the present invention, in which Fig. 4A is a view showing a mask region and an aperture region in a light spot on the medium surface, Fig. 4B is a view showing the state of the directions of magnetization of the respective layers, and Fig. 4C is a graph showing the temperature distribution in the track direction; Fig. 5 is a view showing a change in state of magnetization upon information recording in one example of the magneto-optical recording medium of an embodiment of the present invention; Fig. 6 is a graph showing the temperature distribution in the direction of film thickness upon information recording shown in Fig. 5; Fig. 7 is a view showing a change in state of magnetization upon information recording in another example of the magneto-optical recording medium of an embodiment of the present invention; Fig. 8 is a graph showing the temperature distribution in the direction of film thickness upon information recording shown in Fig. 7; Fig. 9 is a sectional view showing an example of the layer structure of the magneto-optical recording medium of an embodiment of the present invention; Fig. 10 is a sectional view showing another example of the layer structure of the magneto-optical recording medium of an embodiment of the present invention; Figs. 11A to 11D are waveform charts showing the intensities of a light beam upon recording and reproduction in the magneto-optical recording medium of an embodiment of the present invention; Fig. 12 is a view showing a change in state of magnetization upon information recording in still another example of the magneto-optical recording medium of an embodiment of the present invention; Fig. 13 is a view showing a change in state of magnetization upon information recording in still another example of the magneto-optical recording medium of an embodiment of the present invention; Fig. 14 is a sectional view showing still another example of the layer structure of the magneto-optical recording medium of an embodiment of the present invention; Fig. 15 is a sectional view showing still another example of the layer structure of the magneto-optical recording medium of an embodiment of the present invention; and Fig. 16 is a graph showing the temperature dependence of interface magnetic wall energy. An embodiment of the present invention will be described in detail hereinafter with reference to the accompanying drawings. A magneto-optical recording medium of the embodiment has a structure having at least a first magnetic layer which is a in-plane magnetization film at room temperature and changes to a perpendicular magnetization film upon temperature rise, and a second magnetic layer which is a perpendicular magnetization film (Fig. 1), or having a third magnetic layer which has a Curie temperature lower than those of the first and second magnetic layers between the first and second magnetic layers (Fig. 2). The first, second, and third magnetic layers will be respectively referred to as reproducing, recording, and intermediate layers hereinafter. The reproducing layer is set to have a composition so that the layer is an in-plane magnetization film at room temperature, and becomes a perpendicular magnetization film at high temperatures. For this purpose, for example, a composition having a compensation temperature between room temperature and the Curie temperature, large Ms (saturation magnetization) at room temperature, and small Ms at a reproducing temperature is selected. In this case, the reproducing layer is an in-plane magnetization film at room temperature since demagnetizing energy 2πMs 2 is large. However, the reproducing layer becomes a perpendicular magnetization film at the reproducing temperature since Ms becomes small, and perpendicular magnetic anisotropic energy becomes dominant over the demagnetizing energy. As the material of the reproducing layer, a rare earth-iron group amorphous alloy such as GdCo, GdFeCo, GdTbFeCo, GdDyFeCo, NdGdFeCo, or the like is preferable. By adding a light rare earth element such as Nd, Pr, Sm, or the like, a reproduction output for short-wavelength light can be improved. As the recording layer, a film which has large perpendicular magnetic anisotropy and can stably hold a magnetization state, e.g., a rare earth-iron group amorphous alloy film consisting of, e.g., TbFeCo, DyFeCo, TbDyFeCo, or the like; a garnet film; a platinum group-iron group periodic structure film such as Pt/Co, Pd/Co, or the like; a platinum group-iron group alloy film consisting of, e.g., PtCo, PdCo, or the like; or the like is preferable. An element for improving corrosion resistance such as Cr, Al, Ti, Pt, Nb, or the like may be added to the reproducing layer and the recording layer. As the material of the intermediate layer, for example, a rare earth-iron group amorphous alloy such as GdFeCo, GdTbFeCo, GdDyFeCo, TbFeCo, DyFeCo, DyTbFeCo, or the like is preferable. The recording layer and/or recording layer must consist of a ferrimagnetic member, and the directions of magnetization of these layers must be anti-parallel to each other in a state wherein these layers are exchange-coupled at least during recording. For example, when a ferrimagnetic rare earth (RE) iron group element (TM) amorphous alloy is used in the reproducing layer and the recording layer, the composition of the reproducing layer is selected to have dominant rare earth element sublattice magnetization at the recording temperature, and the composition of the recording layer is selected to have dominant iron group element sublattice magnetization at the recording temperature; or vice versa (the arrangement constituted by these layers is normally called an anti-parallel arrangement). Furthermore, in addition to the above-mentioned three layers, in order to enhance the interference effect, a layer consisting of a dielectric such as SiN, AlO x , TaO x , SiO x , or the like may be arranged. Also, in order to improve thermal conductivity, a layer consisting of, e.g., Al, AlTa, AlTi, AlCr, Cu, or the like may be arranged. Furthermore, in order to adjust the exchange-coupling force or magnetostatic coupling force, auxiliary layers such as a recording auxiliary layer, a reproducing auxiliary layer, and the like may be arranged. Moreover, a protective coat consisting of the dielectric layer or a polymer resin may be provided as a protective layer. The recording/reproduction process of the embodiment of the present invention will be described below. Figs. 3A to 3C and Figs. 5 and 6 are associated with a recording medium without an intermediate layer, and Figs. 4A to 4C and Figs. 7 and 8 are associated with a recording medium with an intermediate layer. The reproduction method of a recording signal will be explained below. Upon reproduction, a light beam is irradiated onto the medium, and at this time, the temperature of the irradiated portion rises. Since the medium moves at a constant speed, the temperature distribution on the medium has a pattern extending in the moving direction of the medium, as shown in Figs. 3C and 4C, and includes a high-temperature portion in a local region in the light spot. When the reproducing layer is set to transit from an in-plane magnetization film to a perpendicular magnetization film at a low-temperature portion temperature Tr or higher, a state wherein only the high-temperature portion as the local region of the light spot of the reproducing layer becomes a perpendicular magnetization film portion, and most of the remaining portion remains to be an in-plane magnetization film portion is realized, as shown in Figs. 3B and 4B. Since the reproducing layer portion which has become a perpendicular magnetization film portion is magnetically coupled to the recording layer by exchange-coupling, the magnetization of the recording layer is transferred to the reproducing layer portion. The transferred magnetic signal is converted into an optical signal by the magneto-optical effect of the reproducing layer upon detection of reflected light, and the optical signal is detected. Therefore, as shown in Figs. 3A and 4A, since a portion of the light spot becomes an aperture region for transferring the magnetization of the recording layer, and the remaining portion becomes a mask region for optically shielding magnetization information of the recording layer, a signal having a period equal to or smaller than the diffraction limit of light can be reproduced. Therefore, in the magneto-optical recording medium and the reproduction method, magnetic super-resolution can be achieved without using an initialization magnetic field and a reproducing magnetic field. In the above description, the reproducing layer and the recording layer are magnetically coupled to each other by the exchange-coupling effect. Alternatively, the recording layer and the reproducing layer may be magnetically coupled by magnetostatic coupling upon reproduction. A method of overwriting new binary information on old information by irradiating a light beam, whose light intensity is modulated to two levels, i.e., high level (PH) and low level (PL) in accordance with recording information, onto the magneto-optical recording medium will be described below with reference to Figs. 5 to 8. In the magneto-optical recording medium of the embodiment of the present invention, the reproducing layer and the recording layer constitute an anti-parallel arrangement in a state before the magnetization of the recording layer is stably held, and binary recording is attained by aligning the direction of magnetization of the recording layer in the direction of an external magnetic field or in a direction to be exchange coupled to the reproducing layer by two-level light intensity modulation upon recording. The power values of light beams corresponding to two levels selected in accordance with recording information upon recording (of these beams, a light beam of low recording power will be referred to as PL light hereinafter, and a light beam of high recording power will be referred to as PH light hereinafter) must be set to be larger than that of a reproducing beam Pr, as shown in Fig. 11A, and these two beam power values must have a certain difference therebetween so as not to cause a recording error in consideration of variations of the powers of the light beams. Fig. 5 shows the transition of magnetization states of the respective layers in a case wherein the reproducing layer consists of a rare earth-iron group transition metal amorphous alloy in which the rare earth element sublattice magnetization is dominant, and the recording layer consists of a rare earth-iron group transition metal amorphous alloy in which the iron group element sublattice magnetization is dominant. Fig. 6 shows the temperature distributions in the direction of film thickness when the medium temperature reaches a temperature at which the magnetization of the recording layer is stably held in a cooling process after irradiation of low recording power or high recording power. A case (first type recording) will be explained below wherein PL light is irradiated while applying an external (bias) field Hb (for example, an upward magnetic field). When PL light is irradiated in magnetization states (a) and (b) in Fig. 5, the temperature of the irradiated portion of the reproducing layer rises, the irradiated portion becomes a perpendicular magnetization film portion, and the direction of magnetization of this portion follows the direction of the bias magnetic field Hb, as shown in a state (e) in Fig. 5. At the same time, the temperature of the irradiated portion of the recording layer reaches a temperature near the Curie temperature. Thereafter, when the direction of magnetization of the irradiated portion of the recording layer is aligned in the direction of the bias magnetic field in a temperature drop process, a magnetic wall is formed between the reproducing layer and the recording layer. If the influence of the exchange-coupling force by this magnetic wall is set to be smaller that of the bias magnetic field, the direction of magnetization of the irradiated portion of the recording layer is aligned in the direction of the bias magnetic field and remains stable, as shown in a state (g) in Fig. 5. The condition of this process can be expressed by the following formula (I): σ w /(2Ms 2 •h 2 ) - Hc 2 < Hb where σ w is the magnetic wall energy between the reproducing layer and the recording layer, Ms 2 is the saturation magnetization of the recording layer, h 2 is the film thickness of the recording layer, and Hc 2 is the coercive force of the recording layer. In this manner, upward magnetization is recorded in the irradiated portion of the recording layer, the irradiated portion of the reproducing layer becomes an in-plane magnetization film, and the medium temperature returns to room temperature (RT) (state (c) in Fig. 5). A case (second type recording) will be explained below wherein PH light is irradiated while applying the bias magnetic field Hb. When PH light is irradiated from the magnetization states (a) and (b) in Fig. 5 as in the above-mentioned case, the irradiated portion of the reproducing layer becomes a perpendicular magnetization film, and the direction of magnetization of this portion follows the direction of the bias magnetic field in the same manner as in the above-mentioned case upon irradiation of PL light, as shown in a state (f) in Fig. 5. The medium is then cooled, and the temperature of the irradiated portion of the recording layer drops to a temperature upon irradiation of PL light. However, when PH light is irradiated, the time period from the irradiation of light until the temperature of the irradiated portion of the recording layer drops to the Curie temperature is long. For this reason, during this time period, heat radiation is caused in the direction of film thickness, and the temperature difference between the reproducing layer and the recording layer becomes almost zero (or is smaller than that upon irradiation of PL light ((b) → (c) → (d) of Fig. 6). Therefore, the interface temperature (to be referred to as TH hereinafter) between the reproducing layer and the recording layer in a state wherein the temperature of the irradiated portion of the recording layer drops to the Curie temperature after irradiation of PH light, and the magnetization of the recording layer is generated and held becomes lower than the interface temperature (to be referred to as TL hereinafter) in the same case upon irradiation of PL light. The interface magnetic wall energy has a relationship with the interface temperature, as shown in Fig. 16. For this reason, the interface magnetic wall energy becomes large (σ w *) upon irradiation of PH light, and becomes small (σ w ) upon irradiation of PL light. For this reason, upon irradiation of PH light, an effective magnetic field by exchange-coupling can be increased as compared to that upon irradiation of PL light. Therefore, as shown in a state (h) in Fig. 5, the direction of magnetization of the irradiated portion of the recording layer is not oriented in the direction of the bias field, and the recording layer is exchange-coupled to the reproducing layer, thus forming downward magnetization in the irradiated portion of the recording layer. The condition of this process is expressed by the following formula (II): σ w */(2Ms 2 *•h 2 *) - Hc 2 * > Hb where σ w * is the magnetic wall energy between the reproducing layer and the recording layer at that time, Ms 2 * is the saturation magnetization of the recording layer, h 2 * is the film thickness of the recording layer, and Hc 2 * is the coercive force of the recording layer. In this manner, the downward magnetization is recorded in the irradiated portion of the recording layer, the irradiated portion of the reproducing layer becomes an in-plane magnetization film, and the medium temperature returns to room temperature (RT) (state (d) in Fig. 5). A case will be explained below wherein the characteristics of the magneto-optical recording medium are improved by providing an intermediate layer in the medium. In this case, the reproduction and recording methods are basically the same as those in the above-mentioned two-layered structure. Note that the intermediate layer is located between the reproducing layer and the recording layer, and its Curie temperature Tc I is set to satisfy the following formula (III): TH < Tc I < TL In this manner, the exchange-coupling force acts between the reproducing layer and the recording layer upon irradiation of PH light, and no exchange-coupling force acts upon irradiation of PL light. For this reason, the difference between the influences of the effective magnetic fields by the exchange-coupling force upon irradiation of PL light and PH light can be rendered more distinct, and hence, reliable overwrite recording can be realized. Fig. 7 is a view showing transitions of magnetization states when the intermediate layer is arranged, and Fig. 8 is a graph showing the temperature in the direction of film thickness. In the above description, TH is lower than TL. However, TH may be set to be higher than TL if the film thickness of each magnetic layer is decreased as much as possible, and heat is allowed to diffuse sufficiently in the direction of film thickness by arranging a thermal conduction layer at a side opposite to the light incidence side of the magnetic layers or by setting the moving speed of the light beam to be lower than the heat diffusion speed, as shown in Figs. 9 and 10, and if PH light is irradiated as a time pulse beam, as shown in Fig. 11B, new pulse light is irradiated within a short period of time after irradiation, as shown in Fig. 11C, or PH light is irradiated stepwise, as shown in Fig. 11D. In this case, the magnetization of the recording layer is exchange-coupled to the reproducing layer upon irradiation of PL light, and its direction is oriented in the direction of the bias magnetic field upon irradiation of PH light, opposite to the case described above. Therefore, the overwrite processing based on optical modulation can be achieved, as shown in Figs. 12 and 13, except that the direction of magnetization of the recording layer generated after irradiation of PL light and PH light is opposite to that in the above-mentioned case. The present invention will be described in more detail below by way of its experimental examples. However, the present invention is not limited to these experimental examples. (Experimental Example 1) Si, Gd, Tb, Fe, Co, and Dy targets were attached to a DC magnetron sputtering apparatus, and a glass substrate having a diameter of 130 mm and a polycarbonate substrate with pregrooves were fixed to a substrate holder arranged at a position separated from the targets by a distance of 150 mm. Thereafter, the interior of a chamber was evacuated by a cryopump to a high vacuum of 1 × 10 -5 Pa or less. During vacuum evacuation, Ar gas was supplied into the chamber to 0.4 Pa, and thereafter, an 800-Å thick SiN dielectric layer, a 400-Å thick GdFeCo reproducing layer, a 400-Å thick TbFeCo recording layer, and a 700-Å thick SiN protective layer were formed in the order named to obtain a sample with the arrangement shown in Fig. 14. Upon formation of each SiN layer, N 2 gas was supplied in addition to Ar gas, and the film was formed by DC reactive sputtering. In this case, the mixing ratio of the Ar gas and N 2 gas was adjusted to obtain a refractive index of 2.15. The composition of the GdFeCo reproducing layer was selected to be RE rich at room temperature, and to have a compensation temperature of 240°C and a Curie temperature of 300°C or higher. The composition of the TbFeCo recording layer was selected to be TM rich at room temperature, and to have a Curie temperature of 180°C. The recording/reproduction characteristics were measured using this magneto-optical recording medium. In an evaluation apparatus, the N.A. of an objective lens was set to be 0.55, the laser wavelength was set to be 780 nm, and the linear velocity was set to be 9 m/s. Before measurement, a magnetic field of 5,000 Oe (400 KA/m) was applied in the erasing direction, and thereafter, a magnetic field of 500 Oe (40 KA/m) was applied in the recording direction, thereby recording a signal of 7.5 Mhz by recording power of 13 mW to have a mark length of 0.60 µm. After recording, the power of PL light was set to be 7 to 8 Mw, the power of PH light was set to be 10 to 13 Mw, and a signal of 5.8 Mhz was overwrite-recorded by the optical modulation method to have a mark length of 0.78 µm while applying a bias magnetic field of 800 Oe (80 KA/m). After recording, the reproducing power was set to fall within a range from 2.4 to 3.0 Mw, and the C/N ratio of the new signal of 5.8 Mhz was measured. Then, the recording frequency was changed to 9.8 Mhz, a signal having a mark length of 0.46 µm, which was equal to or smaller than the diffraction limit, was recorded, and the C/N ratio was similarly measured. Also, the C/N ratio of the old signal of 7.5 Mhz was measured. Table 1 shows the measurement results. (Experimental Example 2) Using the same apparatus and method as in Experimental Example 1, an 800-Å thick SiN dielectric layer, a 400-Å thick GdTbFeCo reproducing layer, a 400-Å thick TbFeCo recording layer, and a 700-Å thick SiN protective layer were formed on a polycarbonate substrate in the order named, thus obtaining a sample with the arrangement shown in Fig. 14. The composition of the GdTbFeCo reproducing layer was selected to be RE rich at room temperature, and to have a compensation temperature of 235°C and a Curie temperature of 300°C or higher. The composition of the TbFeCo recording layer was selected to be TM rich at room temperature, and to have a Curie temperature of 200°C. The recording/reproduction characteristics of this magneto-optical recording medium were evaluated as in Experimental Example 1. Table 1 shows the evaluation results. (Experimental Example 3) Using the same apparatus and method as in Experimental Example 1, a 900-Å thick SiN dielectric layer, a 400-Å thick GdDyFeCo reproducing layer, a 300-Å thick TbFeCo recording layer, and a 700-Å thick SiN protective layer were formed on a polycarbonate substrate in the order named, thus obtaining a sample with the arrangement shown in Fig. 14. The composition of the GdDyFeCo reproducing layer was selected to be RE rich at room temperature, and to have a compensation temperature of 225°C and a Curie temperature of 300°C or higher. The composition of the TbFeCo recording layer was selected to be TM rich at room temperature, and to have a Curie temperature of 185°C. The recording/reproduction characteristics of this magneto-optical recording medium were evaluated as in Experimental Example 1. Table 1 shows the evaluation results. (Experimental Example 4) Using substantially the same apparatus and operations as in Experimental Example 1, except that a 50-Å thick GdFeCo intermediate layer was formed between the reproducing layer and the recording layer, a magneto-optical recording medium with the arrangement shown in Fig. 15 was prepared. The composition of the GdFeCo reproducing layer was selected to be RE rich at room temperature, and to have a compensation temperature of 250°C and a Curie temperature of 300°C or higher. The composition of the GdFeCo intermediate layer was selected to be RE rich at room temperature, and to have a Curie temperature of 190°C. The composition of the TbFeCo recording layer was selected to be TM rich at room temperature, and to have a Curie temperature of 208°C. Using this magneto-optical recording medium, the C/N ratio of the new signal of 5.8 Mhz and the C/N ratio of the old signal of 7.5 Mhz were measured following the same procedures as in Experimental Example 1. Thereafter, a signal of 9.8 Mhz was similarly recorded by the optical modulation overwrite method to have a mark length of 0.46 µm, and the C/N ratios of the new and old signals were measured. Table 1 shows the measurement results. (Experimental Example 5) Using the same apparatus and method as in Experimental Example 4, an 800-Å thick SiN dielectric layer, a 400-Å thick GdTbFeCo reproducing layer, a 60-Å thick GdFeCo intermediate layer, a 400-Å thick TbFeCo recording layer, and a 700-Å thick SiN protective layer were formed on a polycarbonate substrate in the order named, thus obtaining a sample with the arrangement shown in Fig. 15. The composition of the GdTbFeCo reproducing layer was selected to be RE rich at room temperature, and to have a compensation temperature of 250°C and a Curie temperature of 300°C or higher. The composition of the GdFeCo intermediate layer was selected to be RE rich at room temperature, and to have a Curie temperature of 195°C. The composition of the TbFeCo recording layer was selected to be TM rich at room temperature, and to have a Curie temperature of 220°C. The recording/reproduction characteristics of this magneto-optical recording medium were evaluated as in Experimental Example 4. Table 1 shows the evaluation results. (Experimental Example 6) Using the same apparatus and method as in Experimental Example 4, a 900-Å thick SiN dielectric layer, a 400-Å thick GdDyFeCo reproducing layer, a 100-Å thick GdFeCo intermediate layer, a 300-Å thick TbFeCo recording layer, and a 700-Å thick SiN protective layer were formed on a polycarbonate substrate in the order named, thus obtaining a sample with the arrangement shown in Fig. 15. The composition of the GdDyFeCo reproducing layer was selected to be RE rich at room temperature, and to have a compensation temperature of 290°C and a Curie temperature of 300°C or higher. The composition of the GdFeCo intermediate layer was selected to be RE rich at room temperature, and to have a Curie temperature of 210°C. The composition of the TbFeCo recording layer was selected to be TM rich at room temperature, and to have a Curie temperature of 250°C. The recording/reproduction characteristics of this magneto-optical recording medium were evaluated as in Experimental Example 4. Table 1 shows the evaluation results. (Comparative Example 1) Using the same apparatus and method as in Experimental Example 1, a 900-Å thick SiN dielectric layer, an 800-Å thick TbFeCo recording/reproducing layer, and a 700-Å thick SiN protective layer were formed in the order named on a glass substrate, thus obtaining a magneto-optical recording medium. The refractive index of each SiN layer was set to be 2.1. The composition of the TbFeCo recording/reproducing layer was selected to be TM rich at room temperature, and to have a saturation magnetization of 200 emu/cc and a Curie temperature of 220°C. The recording/reproduction characteristics of this magneto-optical recording medium were evaluated as in Experimental Example 1. Table 1 shows the evaluation results. Recording Frequency of New Signal 5.8 MHz 9.8 MHz Reproduced Signal New Signal C/N Old Signal C/N New Signal C/N Old Signal C/N Unit dB dB dB dB Experimental Example 1 48 5 40 5 Experimental Example 2 2 49 6 41 5 Experimental Example 3 3 49 4 39 6 Experimental Example 4 48 2 43 2 Experimental Example 5 5 49 1 42 2 Experimental Example 6 49 3 43 1 Comparative Example 1 19 22 8 21 (old signal = 7.5 MHz) As can be seen from this table, upon comparison between the characteristics of the magneto-optical recording media in accordance with the present invention of Experimental Examples 1 to 6 with those of the conventional magneto-optical recording medium of Comparative Example 1, optical modulation overwrite can be realized and at the same time, a signal with a small mark length can be satisfactorily reproduced in the media of the present invention. Using the magneto-optical recording medium and the recording/reproduction method, recording based on optical modulation overwrite and reproduction of a magnetic domain smaller than the beam spot size can be realized using a simple apparatus with no initialization magnet without complicating the layer structure of the medium, thus achieving high-density recording.

Claims: A method of recording information onto a magneto-optical recording medium, the magneto-optic recording medium comprising a stack of first and second magnetic layers, the first magnetic layer having an in-plane magnetization state at room temperature and a perpendicular to the plane magnetization state in a first temperature range between room temperature and the Curie temperature of the first magnetic layer; and the second magnetic layer having a Curie temperature between room temperature and the Curie temperature of the first magnetic layer, and a perpendicular to the plane magnetization state in a second temperature range between room temperature and the Curie temperature of the second magnetic layer, wherein the first and second magnetic layers are such that when the first and second magnetic layers both have a perpendicular magnetization state the preferred direction of magnetization of the first magnetic layer is anti-parallel to that of the second magnetic layer, the recording method comprising the steps of: applying a bias magnetic field (H b ) to the medium, and irradiating successive portions of the medium with a light beam of either a first power (P L ) or a second power (P H ) dependent on information to be recorded, the method being characterised in that in the irradiating step the light beam at the first power (P L ) is arranged to raise the temperature of a portion of the medium to a first temperature, the first temperature being not less than the Curie temperature of the second magnetic layer, at which the direction of magnetization of the first magnetic layer aligns parallel to the direction of the bias magnetic field and the magnetization of the second magnetic layer disappears, and such that after the subsequent reduction in temperature to a temperature at which the magnetization of the second magnetic layer reappears, the interface domain energy between the first magnetic layer and the second magnetic layer is small enough to allow the direction of the magnetization of the second magnetic layer to align parallel to the direction of the bias magnetic field; and the light beam at the second power (P H ) is adapted to raise the temperature of a portion of the medium to a second temperature, the second temperature being higher than the first temperature and within said first range, at which the direction of magnetization of the first magnetic layer aligns parallel to the direction of the bias magnetic field and the magnetization of the second magnetic layer disappears, and such that after the subsequent reduction in temperature to a temperature at which the magnetization of the second magnetic layer reappears, the interface domain energy between the first layer and the second layer is large enough such that the direction of the magnetization of the second magnetic layer is aligned anti-parallel to the direction of the bias magnetic field. A method according to claim 1, wherein the first and second light beam powers are effective to cause said change in the magnetization of the first magnetic layer in only a part of the region of the medium irradiated by the light beam. A method according to either claim 1 or claim 2 wherein in the irradiating step the light beam is incident on the medium from the first magnetic layer side of the stack of first and second magnetic layers. A system for recording information onto a magneto-optical recording medium, said system comprising a recording apparatus and a magneto-optical recording medium, the magneto-optic recording medium comprising a stack of first and second magnetic layers, the first magnetic layer having an in-plane magnetization state at room temperature and a perpendicular to the plane magnetization state in a first temperature range between room temperature and the Curie temperature of the first magnetic layer; and the second magnetic layer having a Curie temperature between room temperature and the Curie temperature of the first magnetic layer, and a perpendicular to the plane magnetization state in a second temperature range between room temperature and the Curie temperature of the second magnetic layer, wherein the first and second magnetic layers are such that when the first and second magnetic layers both have a perpendicular magnetization state the preferred direction of magnetization of the first magnetic layer is anti-parallel to that of the second magnetic layer, and the recording apparatus comprising: means for applying a bias magnetic field to the medium; and means for irradiating successive portions of the medium with a light beam of either a first power (P L ) or a second power (P H ) dependent on information to be recorded, the system being characterized in that: the light beam at the first power (P L ) is adapted to raise the temperature of a portion of the medium to a first temperature, the first temperature being not less than the Curie temperature of the second magnetic layer, at which the direction of magnetization of the first magnetic layer aligns parallel to the direction of the bias magnetic field and the magnetization of the second magnetic layer disappears, and such that after the subsequent reduction in temperature to a temperature at which the magnetization of the second magnetic layer reappears, the interface domain energy between the first magnetic layer and the second magnetic layer is small enough to allow the direction of the magnetization of the second magnetic layer to align parallel to the direction of the bias magnetic field; and the light beam at the second power (P H ) is adapted to raise the temperature of a portion of the medium to a second temperature, the second temperature being higher than the first temperature and within said first range, at which the direction of magnetization of the first magnetic layer aligns parallel to the direction of the bias magnetic field and the magnetization of the second magnetic layer disappears, and such that after the subsequent reduction in temperature to a temperature at which the magnetization of the second magnetic layer reappears, the interface domain energy between the first layer and the second layer is large enough such that the direction of the magnetization of the second magnetic layer is aligned anti-parallel to the direction of the bias magnetic field. A system according to claim 4, wherein said irradiating means is adapted such that the first and second light beam powers are effective to cause said change in the magnetization of the first magnetic layer in only a part of the region of the medium irradiated by the light beam. A system according to either claim 4 or claim 5, wherein said irradiating means is operable to emit a light beam at a third power for reproduction of information recorded on the magneto-optical recording medium.

Inventors: NISHIMURA NAOKI, NISHIMURA, NAOKI, NISHIMURA, NAOKI, C/O CANON K.K.
Applicants: CANON KK, CANON KABUSHIKI KAISHA
Application year: 1995
Main classification: G11B11
IPC codes: G11B11