At the A site, the wide variety of doped elements give differing magnetic moments, valence states, and ionic radii. This generates a mixed valence state of Mn³⁺ and Mn⁴⁺, which makes it possible to pass the DE at low temperatures and produce ferromagnetism. At the same time, the average ionic radius of the A-site ions, crystal structure, and magnetic moment of the molecules change. This affects the DE and MCE of the material while producing a wealth of magnetic order phenomena, such as the charge order, orbit order, and mutual coupling. After A-site doping, the internal DE and molecular magnetic moment of the material strongly influence the Curie temperature (Tc) and maximum magnetic entropy ( Δ S M max ).

Based on the selected substrate RaMnO₃ (Ra=La, Nd, Pr, Sm, such as LaMnO₃), has been found to have better magnetocaloric properties in the room temperature range (Phan and Yu, 2007; Sun et al., 2017), especially in low and medium magnetic fields, which has a larger magnetic entropy change than that of Gd and GdSiGe alloy phases.

The types of ion doping can be divided into single-, multi-ion doping. Single-ion doping generally uses Na, Sr, Ag, Ca, Cd, Ba, and K plasmas at the A site, as shown in Table 1. The study found that under the same valence state, different doping ion radii have different effects on the structure and magneto-caloric properties of LaMnO₃. Zhong et al. (1998), Zhong et al. (1999), Das and Dey (2007) studied La_1-xNa_xMnO₃ (0 < x < 0.15) and La_1-xK_xMnO₃ (0 < x < 0.2) materials, they found that under the conditions of the same magnetic field changes, Δ S M of the material increases with the increase of Na⁺, K⁺ doping amount. It’s Tc also rises, when the K doping amount x = 0.2, its Δ S M becomes 2.2 J/(kg K), and its Tc also rises to 350 K.While Li⁺ doping will decrease Magnetic change and Tc of perovskite manganite (Ghosh and Ghatak, 2016). It can be concluded that the A-site doping of low-valence ions significantly affects the magnetic entropy change and Tc, and there is often an extreme value, which should be related to the effect of doping on Mn³⁺/Mn⁴⁺ in the material system.

At the same time, the study found that the addition of alkaline earth metal or alkali metal ions that are lower in value than La in the A site has a significant change in the performance of LaMnO₃. Mcbride et al. (2016), Demin and Koroleva (2004) and others have carried out research on the A-site Sr²⁺ doping of LaMnO₃. They believe that the A-site doping of Sr²⁺ with a slightly larger radius than La³⁺ will cause the lattice structure to deviate from the ideal cubic structure, thereby producing Mn-O The bond length and Mn³⁺-O^2--Mn⁴⁺ bond angle changes, the overlap of electron orbits increases the DE and the MCE. With the increase of Sr²⁺content, the magnetic entropy change of La_1-xSr_xMnO₃ (0.1 < x < 0.3) increases, and Tc also increases, Δ S M max = 1.7 J/(kg K), and Tc is about 350–360 K. Bohigas et al. (2000), Sun et al. (2000) studied the change of the MCE of La_0.6Ca_0.4MnO₃. Under the same magnetic field change condition, with the increase of Ca²⁺ doping, the material Δ S M first increased and then decreased. Hussain et al. (2016) studied the MCE of La_0.6Ba_0.4MnO₃ and revealed that the MCE first increased and then decreased with the increase of Ba²⁺ doping. When the doping amount exceeds 0.3, both the Δ S M and the Tc are reduced. The performance of the material is also related to the influence of the size of the doped ions on the symmetry of the crystal structure of the material, which is related to the effect of the Jahn-Teller effect on the performance of the material. When the size of the doped ions is too large or too small, the lattice distortion is intense, the Mn³⁺/Mn⁴⁺ distribution period is affected and the DE is weakened.

When multi-ion doping, the effect of doping behavior on the magnetocaloric properties and Tc of perovskite manganite is more complicated. One study found that La_0.65Sr_0.35MnO₃ (Phan et al., 2003) with an applied magnetic field of 1 T has Tc = 305 K, which is close to room temperature. The Δ S M becomes 2.12 J/(kg K) and RCP = 106 J/kg, therefore researchers usually utilize La_0.65Sr_0.35MnO₃ for further ion doping research. For example, Kong (Kong and Zou, 2018) doped Gd and Na at the A site. It is found that the Tc of multi-ion doping gradually decreases to around room temperature with the increase of the doping amount of Gd and Na ions. The DE has a close relationship with the doping content. On the basis of LaMnO₃, the Mn⁴⁺will substitute the Mn³⁺, when the Alkaline earth metal ions access to this system. Moreover, the ratio of Mn³⁺/Mn⁴⁺ is considered changed along with the content of doping ions. Linh et al. (2017) studied the Δ S M change and the Tc of La_0.7Ca_0.3-xA_xMnO₃ and found that the Tc of the material gradually rises with the increase of Sr and Ba ion doping during multi-ion doping, but it will reduce the Δ S M of the material. Duc, Nguyen Thi My (Duc et al., 2019) studied the (La_0.5Pr_0.5)_0.6Ba_0.4MnO₃ material and found that with the doping of Pr, the Δ S M of the material will increase to a certain extent, but the Tc will be reduced Temperature. The ions doped at the A site changed the ratio of Mn³⁺/Mn⁴⁺ for the matrix material and the average ion radius of the A site, which led to change in the mismatch factor. The DE was reduced, and the Tc will dropped to a certain extent.

In the study of magnetic refrigeration, Dagotto divided perovskite manganite into wide-, medium- and small-bandwidth types based on the bandwidth of the DE (Dagotto et al., 2001). La_0.65Sr_0.35MnO₃ material belongs to the wide-bandwidth type, and another important perovskite manganite of Pr_1-xSr_xMnO₃ belongs to the small-bandwidth type. The ferromagnetic-antiferromagnetic and paramagnetic-ferromagnetic transitions appear in the magnetic phase diagram simultaneously for x between 0.5 and 0.55 (Pollert et al., 2002). In this T range, as the Sr content at the A site increases, Tc gradually decreases, and the Neel temperature (critical temperature of antiferromagnetic-paramagnetic transition) increases with the two transitions when reaching a certain value (Martin et al., 1999). This shows that Sr²⁺ doping at the A site causes changes in the ratio of Mn ions, which affects the DE and phase change of the material. Since the 21st century, researchers have performed increasing studies on Pr_1-xSr_xMnO₃. Bingham (Caballeroflores et al., 2014) found that Pr_0.5Sr_0.5MnO₃ has a significant anomalous MCE. When the external magnetic field is 5 T, Δ S M = 6.8 J/(kg K). Biswas et al. (2014) found that the charge ordering degree of Pr_0.5Sr_0.5MnO₃ is very closely related to the size of the particles and has no effect on the Tc and DE.

To maintain the balance of the valence state after doping, A-site doping indirectly changes the ratio and content of Mn³⁺/Mn⁴⁺, changes the structure of the perovskite manganite, and affects its DE and rich physical properties (magnetic, electrical, etc.). As Mn³⁺-O^2--Mn⁴⁺ is the basis of DE, the magnetic properties of ABO₃ perovskite structures are usually produced based on B-site ions; thus, B-site doping directly affects the ratio of Mn³⁺/Mn⁴⁺. At the same time, other magnetic ions introduced by doping increase the abundance and complexity of the DE between B-site ions. Therefore, a small amount of doping is performed at the B-site to change the Tc and increase the magnetic moment of the site to increase the Δ S M .

B-site can be doped with transition metals (Ni, V, Fe, Co, Cr, Cu). Kong (2018) doped Ni and V at the B site for La_0.65Sr_0.35MnO₃. When doped with Ni, the Tc decreased significantly with the doping content, which moved below room temperature. When the B site was doped with V, Tc showed an increasing trend, but the Δ S M was relatively low (Kong, 2018). The La_0.67Pb_0.33Mn_1−xCo_xO₃ (0.15 ≤ x ≤ 0.3) material studied by N. Dhahri (Abdouli et al., 2019), with the increase of Co ion content, the Δ S M of the material has been increased to 3.1 J/(kg K), but it caused the Tc to drop drastically to about 250 K. Phan (Phan and Yu, 2007) found that when the external magnetic field of La_0.67Sr_0.33Mn_0.9Cr_0.1O₃ is 5T, its Tc = 328 K is higher than room temperature, and Δ S M = 5 J/(kg K). Lu (Lu et al., 2006) found that when Mo trace elements are doped in LaMnO₃, they replace the Mn sites to produce Mn²⁺, which result in the DE of Mn²⁺-O^2--Mn³⁺and exhibits ferromagnetism.

Studies have found that after perovskite manganese oxide is doped at the B site and is placed under an external magnetic field, the Tc and Δ S M changes are much lower than those after A-site doping. This is because the magnetic nature of perovskite manganese oxides and the MCE are primarily by DE, which are based on the movement of external electrons outside in Mn³⁺-O^2--Mn⁴⁺.

The main reasons why the doping effect of the B site is lower than that of the A site are as follows. 1) Changes in Tc depend directly on the DE, and mixed interactions occur after the B site is doped with ions. At greater doping contents and, after the doping ions replace the Mn sites, the DE between Mn³⁺-O^2--Mn⁴⁺ decreases due to the increased super-exchange between doping and the surrounding ions, which causes the Tc to decrease. 2) After the B -sites are doped, the doping ions replace one of the Mn³⁺-O^2--Mn⁴⁺ ions in the double exchange, such as Co ions. The diverse spin electronic states and complex valence states of Co ions produce complex DE. Thus, Co doping is considered to as a partial replacement of Mn ions for DE. When Co ions replace Mn, antiferromagnetic super exchange channels (Co³⁺-O^2--Mn⁴⁺, Co²⁺-O^2--Co⁴⁺) and ferromagnetic double exchange channels (Mn³⁺-O^2--Mn⁴⁺, Co³⁺-O²-Co⁴⁺) form in the system (Ghosh et al., 1999). Thus, antiferromagnetic double exchange interactions and ferromagnetic double exchange interactions coexist. As antiferromagnetic and ferromagnetic exchanges coexist, as the doped Co ions content increases and the long-range ferromagnetic order of the sample is replaced with ferromagnetic cluster behaviors (Chainani et al., 1992). This result in spin magnetic moment direction. The deviation and chaotic magnetic moment of the spin result in an overall decreased magnetic moment and Δ S M .

During ion doping modification, more consideration should be given to doping at the A site of the perovskite manganese oxide to indirectly change the proportion of manganese ions to affect the crystal structure and physical properties of the perovskite manganese oxide.

The crystal structure of perovskite manganese oxides can be changed through doping. Thus, research has been conducted to determine the impact of vacancy doping. Holes are divided into two categories: oxygen and elements. However, the generation of oxygen holes reduces DE of the material, while the Tc and Δ S M of the material decrease (Xu). In element holes, researchers have discovered the giant magnetoresistance effect and giant MCE in La_0.9MnO₃ (Patra et al., 2009).

The Tc of the La_0.925-xMnO₃ prepared by Xu (Xu) decreased with x. La_0.925-xMnO₃ was also affected by the decreased Tc due to the ionic radius of the A site and the increased Mn⁴⁺ content, which led to an increased Tc. the large La_0.925-xMnO₃ ion vacancy concentration causes significant lattice distortion, and a smaller A-site ion radius is the main factor controlling the decrease in Tc.

La_1-xCa_xMnO₃ has a high magnetic entropy change and a relatively low Tc, which can be increased by doping. La_1-xCa_xMnO₃ replaces La³⁺ with Ca²⁺. To balance the valence, Mn⁴⁺ needs to be produced, which further modifies the magnetization and Tc of the material. Changes in the valence state of Mn ions can alter the magnetic properties of the material from ferromagnetic to paramagnetic. There are two energy levels for Mn ions. The principle of the lowest energy, high energies into two orbitals, which causes crystal lattice distortion. This system has therefore become a refrigeration material that is widely studied by scientific researchers. He (He, 2019) used the sol-gel method to prepare La_0.65-xCa_0.35MnO₃ (0 ≤ x ≤ 0.15). The experimental results show that as the La³⁺ vacancy concentration increases, the ion radius and the mismatch factor change. The Tc of La_0.65-xCa_0.35MnO₃ also gradually increases. When the external magnetic field is 0–5 T, Δ S M = 1.17 J/(kg K). This is because there are four electrons in the outermost layer of Mn³⁺, of which three are in the t_2g localized state and the other is in the patrol state and is hybridized with the 2p orbital of the O ion to form a covalent bond. With the increased vacancy concentration, the number of Mn³⁺ ions gradually decreases, the number of Mn⁴⁺ gradually increases, and the concentration of the patrol state into vacancies increases. Thus, the DE of the material increases, and the Tc becomes larger.

Brion (Brion et al., 1999) used the solid phase method to prepare La_1-xMnO₃. The study found that the Tc of La_0.93MnO₃ and La_0.97MnO₃ were 170 and 118 K, respectively, and the Mn⁴⁺ content was 21 and 9%. Brion believed that when x mol of La³⁺ is replaced with a vacancy, 3x mol of Mn³⁺ is converted into Mn⁴⁺. Walha et al. (2009) found that Mn⁴⁺ increased with the vacancy concentration. However, Sankar (Joy et al., 2002) prepared La_1-xMnO₃ using the solid-phase method, which indicated that Tc increased with the vacancy concentration but Mn⁴⁺ decreased. There are different experimental results for Mn⁴⁺ with changes in the vacancy concentration, which manifest in the A site of perovskite manganese oxide. A small amount of AE or RE with a large ion radius can be added when synthesizing samples. To generate cation vacancies, it is first ignored that there are more B-site ions than A-site ions, which can enter A-sites. Tang et al. (2007) researched and proposed the A_1-xBO_3-δ model based on the minimum energy principle and the crystal defects in thermal equilibrium theory. In the model, the A-site gap is larger than the B-site gap. Ions on the lattice points are generated in high-temperature heat-treated samples. The violent thermal movement results in the migration of vacancy defects, and large gaps are first occupied by ions. The lack of A-site ions is compensated by B-site ions (such as Mn). Therefore, vacancies in the sample appear in the A site instead of the B site.